JPS58185477A - High speed cutting ceramic for cutting tool - Google Patents
High speed cutting ceramic for cutting toolInfo
- Publication number
- JPS58185477A JPS58185477A JP57067017A JP6701782A JPS58185477A JP S58185477 A JPS58185477 A JP S58185477A JP 57067017 A JP57067017 A JP 57067017A JP 6701782 A JP6701782 A JP 6701782A JP S58185477 A JPS58185477 A JP S58185477A
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- Prior art keywords
- oxide
- cutting
- orthorhombic
- turconium
- 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.)
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- Compositions Of Oxide Ceramics (AREA)
- Cutting Tools, Boring Holders, And Turrets (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】 この発明は、すぐれた耐摩耗性、耐熱衝撃性。[Detailed description of the invention] This invention has excellent abrasion resistance and thermal shock resistance.
および高温強度を有し、特にこれらの特性が要求される
鋼および鋳鉄の高速切削に切削工具として用いた場合に
すぐれた切削性能を発揮するセラミック材料に関するも
のである。The present invention relates to a ceramic material that has high-temperature strength and exhibits excellent cutting performance when used as a cutting tool for high-speed cutting of steel and cast iron, which particularly require these properties.
近年、鋼および鋳鉄の高速切削を可能とすべく種々の研
究開発が試みられ、なかでも工作機械の高剛性化と切削
工具材料の改善の両面から、これら被削材の高速切削へ
の移行は着々と達成されつつあり、現時点では３００〜
６００ｍ／Ｍの高い切削速度での安定した切削が１つの
目標とされている。なお、前記の３００〜６００ｍ／ｍ
の高い切削速度は、高速切削時に発生する熱に対してす
ぐれた耐酸化性を示すと共に、Ｆｅとの化学的反応性が
低く、かつ摩擦係数の小さな酸化アルミニウム（以下Ａ
Ｎ２０３で示す）を主成分として含有するＡｇ２Ｏ，基
焼結材料を切削工具として使用するという前提で、高速
切削を可能とすべく工作機械に改良を加えることによっ
て達成できるとして定められたものである。In recent years, various research and development efforts have been made to enable high-speed cutting of steel and cast iron, and in particular, the transition to high-speed cutting of these work materials has been attempted from the standpoint of both increasing the rigidity of machine tools and improving cutting tool materials. It is steadily being achieved, and at the moment it is 300~
One goal is stable cutting at a high cutting speed of 600 m/M. In addition, the above-mentioned 300 to 600 m/m
The high cutting speed of aluminum shows excellent oxidation resistance against the heat generated during high-speed cutting, and aluminum oxide (hereinafter referred to as A
It was established that this can be achieved by improving machine tools to enable high-speed cutting, on the premise that Ag2O-based sintered materials containing N203 as the main component are used as cutting tools. .
しかしながら、上記のＡｇ、、ｏ３基焼結材料は、十分
な耐熱衝撃性および高温における機械的強度を備えてい
ないために、これを切削工具として、特に錫ｌのり）削
（ζ３００〜６００ｍ／ｍの高い切削速度で使用した場
合、工作機械の改良も未だ不十分であることと相俟って
、安定した切削性能を発揮しないものである。However, since the above-mentioned Ag, O3-based sintered material does not have sufficient thermal shock resistance and mechanical strength at high temperatures, it is used as a cutting tool, especially for cutting (ζ 300 to 600 m/m When used at high cutting speeds, this combined with the fact that machine tools have not yet been sufficiently improved means that stable cutting performance cannot be achieved.
また、一方、熱膨張係数が小さく、すなわち耐熱衝撃性
にすぐれ、かつ高温における機械的強度にもすぐれた窒
化けい素や、窒化けい素にＡｌ２Ｏ２が固溶したものか
らなるサイアロンを主成分とし、これに酸化イツトリウ
ム（以下Ｙ２Ｏ３で示す）、酸化マグネシウム（以下Ｍ
ｇＯで示す）、酸化けい素。On the other hand, silicon nitride, which has a small coefficient of thermal expansion, that is, excellent thermal shock resistance, and excellent mechanical strength at high temperatures, and sialon, which is a solid solution of silicon nitride with Al2O2, are the main ingredients. In addition to this, yttrium oxide (hereinafter referred to as Y2O3), magnesium oxide (hereinafter referred to as M
gO), silicon oxide.
♀化アルミニウム、酸化チタン、酸化ツルコニウム（以
ｉ’ＺｒＯ２で示す）、および酸化ノ・コニウムのうち
の１棟または２種以上を１〜３０重量％重量音程させた
ものからなる窒化けい素基焼結材料を、鋼および鋳鉄の
高速切削に切削工具として使用する試みもなされたが、
この窒化けい素基焼結材料はＦｅとの反応性が高いため
に、特に鋼の高速切削に際しては摩耗が激しく、切削工
具としては汎用性のきわめて低いものである。Silicon nitride-based sintered material consisting of one or more of aluminum oxide, titanium oxide, turconium oxide (hereinafter referred to as i'ZrO2), and turconium oxide with a pitch of 1 to 30% by weight. Attempts have also been made to use binder materials as cutting tools for high-speed cutting of steel and cast iron;
Since this silicon nitride-based sintered material has high reactivity with Fe, it suffers from severe wear especially during high-speed cutting of steel, and has extremely low versatility as a cutting tool.
そこで、本発明者等は、上述のような観点から。Therefore, the inventors of the present invention, from the above-mentioned viewpoint.
鋳鉄は勿論のこと、鋼の高速切削に際して、すぐれた切
削性能を発揮するのに不可欠な特性、すなわち、すぐれ
た耐摩耗性、耐熱衝撃性、および高温強度を具備した切
削工具材料を得べく研究を行なった結果、非常に高い硬
さと強固な結晶粒子間結合を有するが、結晶変態が約１
１００℃前後で生じるために、刃先が高温になる切削工
具材料には適さないと考えられていたＺ ｒｏ２粉末を
主原料粉末として用い、これにＡｔ ｔＯ３粉末と、Ｙ
２Ｏ３粉末およびＭｇＯ粉末のうちの１種または２種と
、炭化チタン（以下ＴｉＣで示す）粉末、窒化チタン（
以下ＴｉＮで示す）粉末、および炭窒化チタン（以下Ｔ
１ＣＮで示す）粉末のうちの１種または２種以上と、さ
らに必要に応じてＮ１粉末、 Ｃｏ粉末、 Ｍｏ粉末。Research aimed at obtaining cutting tool materials with properties essential to exhibiting excellent cutting performance when cutting not only cast iron but also steel at high speeds, namely excellent wear resistance, thermal shock resistance, and high-temperature strength. As a result, it has very high hardness and strong bonding between crystal grains, but the crystal transformation is about 1
Zro2 powder, which was thought to be unsuitable for cutting tool materials where the cutting edge becomes hot because it is produced at around 100°C, was used as the main raw material powder, and in addition AttO3 powder and Y
One or two of 2O3 powder and MgO powder, titanium carbide (hereinafter referred to as TiC) powder, titanium nitride (
(hereinafter referred to as TiN) powder, and titanium carbonitride (hereinafter referred to as T
1CN) powder, and if necessary, N1 powder, Co powder, and Mo powder.
Ｗ粉末、および炭化タングステン（以下ＷＣで示す）粉
末のうちの１種または２種以上とを配合し、混合した後
、通常のホットプレス法、あるいは真空またはガス雰囲
気中での通常の焼結法にて焼結すると、鋼およびυｊ鉄
の高速切削に適した切削工具田七′ノミンク材料が得ら
れるという知見を得たのである。W powder and one or more types of tungsten carbide (hereinafter referred to as WC) powder are blended and mixed, followed by a normal hot pressing method or a normal sintering method in a vacuum or gas atmosphere. They found that when sintered in a cutting tool, a material suitable for high-speed cutting of steel and υj iron can be obtained.
したがって、この発明は上記知見にもとづいてなされた
ものであって、重量％で、
ＡＭ２ｔ、）３： １０−３０ ％、
Ｙ２Ｌ）３およびｌ・、１ ｇ Ｏのうちの１種または
２種：１〜６％。Therefore, this invention was made based on the above findings, and in weight percent, one or two of AM2t, )3: 10-30%, Y2L)3 and l., 1 g O: 1-6%.
・ｐ １（、’、 、 ’Ｉ’ｌＮ ＋ および’Ｉ
ｌ’１０２のうちの１種または２種以上 ；３〜３０％
を含有し、さらに必要に応じて、
Ｎ１ 、 ＋ｒ＋＋ 、 ＩＶＩＯ、Ｖ／ 、およびＷ
Ｃのうちの１種または２種以上：０．１〜５％を含有し
、
残りが正方晶系ＺｒＯ２と斜方晶系ＺｒＯ２および不可
避不純物からなる組成（ただし前記両Ｚｒ○２の含有量
は３０チ以上）、並びに少なくとも前記Ｚ ｒ Ｏ２の
連続相を有する組織（この場合Ａｅ２０３の含有量が相
対的に高い場合にはＺｒＯ２とＡｇ２Ｏ３の連続相が共
存する）を有し、かつ正方晶系ｚ ｒｏ ２ ／斜方晶
系ＺｒＯ２の重量比；ｌ／９〜９／１を満足する特に高
速切削性能にす七°れた切削工具用セラミック材料に特
徴を有するものである。・p 1(, ', , 'I'lN + and 'I
One or more types of l'102; 3-30%
and, if necessary, N1, +r++, IVIO, V/, and W
One or more of C: 0.1 to 5%, and the remainder consists of tetragonal ZrO2, orthorhombic ZrO2, and inevitable impurities (however, the content of both Zr○2 is 30 or more), and a structure having at least the continuous phase of ZrO2 (in this case, if the content of Ae203 is relatively high, continuous phases of ZrO2 and Ag2O3 coexist), and a tetragonal system. The present invention is characterized by a ceramic material for cutting tools that satisfies the weight ratio of z ro 2 /orthorhombic ZrO2; l/9 to 9/1, and has particularly good high-speed cutting performance.
つぎに、この発明のセラミック材料において、成分組成
範囲を上記の通りに限定した理由を説明する。Next, in the ceramic material of the present invention, the reason why the component composition range is limited as described above will be explained.
（ａ） Ａｔ 、 ｏ ３
Ｍ２Ｏ，成分には材料の高温における安定性および耐摩
伸性を向上させる作用があるが、その含有量が１０チ未
満では前記作用に所望の効果が得られず、一方６０％を
越えて含有させると材料の耐熱衝撃性が急激に劣化する
ようになることから、その含有量を１０〜６０チと定め
た。なお％Ａ９２０３．４０〜６０％を含有した場合、
ＺｒＯ２の連続相と共存した状態で、Ｍ２Ｏ３の連続相
が存在した組織となる。(a) The At, O3M2O, component has the effect of improving the stability at high temperatures and the abrasion elongation resistance of the material, but if its content is less than 10%, the desired effect cannot be obtained; If the content exceeds 60%, the thermal shock resistance of the material will deteriorate rapidly, so the content was set at 10 to 60%. In addition, when containing %A9203.40 to 60%,
A structure is formed in which a continuous phase of M2O3 coexists with a continuous phase of ZrO2.
（ｂ）Ｙ２Ｏ３およびＭｇＯ
これらの成分には、材料におけるＺｒＯ２成分のうちの
正方晶系（高温安定型）のものを安定化させると共に、
ＺｒＯ２およびＭ２Ｏ３粉末の焼結性を一段と向上させ
、さらに結晶粒の成長を抑制し、もって高温強度を向上
させる作用があるが、その含有量が１％未満では前記作
用に所望の効果が得られず、一方６％を越えて含有させ
ると、材料の耐熱衝撃性および耐摩耗性が低下するよう
になることから、その含有量を１〜６％と定めた。(b) Y2O3 and MgO These components stabilize the tetragonal system (high temperature stable type) of the ZrO2 components in the material, and
It has the effect of further improving the sinterability of ZrO2 and M2O3 powders, suppressing the growth of crystal grains, and thereby improving high-temperature strength, but if the content is less than 1%, the desired effect cannot be obtained. On the other hand, if the content exceeds 6%, the thermal shock resistance and abrasion resistance of the material will decrease, so the content was set at 1 to 6%.
（（・）“］’ｉＣ、ｉ’ｉｔＪ 、およびＴ１ＣＮこ
れ１′〕の成分は、いずれも材料中に分散相を形成して
存在すると共に、全率固溶型であることから、“４．Ｉ
ｌｌ２およびＡ＋！２０３と共存した場合には酸素を固
溶し、かつ一部のＺｒを固溶した状態になっている。こ
のようにこれらの成分は、その格子中に酸素と４４ 、
が固溶した硬質分散粒子として存在するために、これら
の１戊分の存在によって材料の耐摩耗性は著しく向上す
るようになるが、その含有量が３％未満では所望の耐摩
耗性を確保することができず、一方３０％を越えて含有
させると、材料のもつすぐれた耐熱′衝撃性が劣化する
ようになることから、その含有量を３〜３０％と定めた
。The components ((・)"]'iC, i'itJ, and T1CNKore1') all exist in the material in the form of a dispersed phase and are completely solid solution type, so "4 .I
ll2 and A+! When it coexists with 203, it is in a state in which oxygen is dissolved in solid solution and some Zr is also dissolved in solid solution. These components thus have oxygen and 44 in their lattice,
Since these exist as hard dispersed particles in solid solution, the wear resistance of the material is significantly improved by the presence of one portion of these, but if the content is less than 3%, the desired wear resistance cannot be achieved. On the other hand, if the content exceeds 30%, the material's excellent heat and shock resistance will deteriorate, so the content was set at 3 to 30%.
（ｄｉ Ｎ＋、 Ｃｏ、 Ｍｏ、 Ｗ、およびＷにれ
らの成分には、焼結を促進し、もって材料を高密度化し
て高温強度を一段と向上させる作用があるので、必要に
応じて含有させるが、その含有量が０１％未満では前記
作用に所望の効果が得られず、一方５チを越えて含有さ
せると耐摩耗性が劣化するようになることから、その含
有量を０１〜５％と定めた。(di N+, Co, Mo, W, and W have the effect of promoting sintering, thereby increasing the density of the material and further improving the high-temperature strength, so they may be included as necessary. However, if the content is less than 0.1%, the desired effect cannot be obtained, while if the content exceeds 5%, the wear resistance will deteriorate. It was determined that
（ｅ） ＺｒＯ２
上記のように、この発明の材料においては、正方晶系Ｚ
ｒＯ２と斜方晶系ＺｒＯ２とが共存し、かつこの両’１
ｒ０２が連続相（ＺｒＯ，の含有量が３０％未満では連
続相の形成は困難であり、したがって連続相形成には３
０チ以上の含有が必要となる）を形成した組織を有する
が、この組織、すなわち正方晶系ＺｒＯ２と斜方晶系Ｚ
ｒＯ２の共存と、前記内ＺｒＯ２による連続相の存在に
よって材料はきわめて高い耐熱衝撃性をもつようになる
のである（この技術的理由は定かではない）。また、前
記内ＺｒＯ２における相互重量比が１７９未満でも、９
／ｌを越えても正方晶系ＺｒＯ２と斜方晶系ＺｒＯ２の
相互重量割合がくずれ、いずれか−力が多くなりすぎ、
他方が少なくなりすぎる結果となって、所望のすぐれた
耐熱衝撃性を確保することができないのである。(e) ZrO2 As mentioned above, in the material of this invention, tetragonal ZrO2
rO2 and orthorhombic ZrO2 coexist, and both '1
If the content of r02 is less than 30%, it is difficult to form a continuous phase.
This structure is composed of tetragonal ZrO2 and orthorhombic ZrO2.
The coexistence of rO2 and the presence of a continuous phase of ZrO2 provide the material with extremely high thermal shock resistance (the technical reason for this is not clear). In addition, even if the mutual weight ratio of ZrO2 in the above is less than 179, 9
/l, the mutual weight ratio of tetragonal ZrO2 and orthorhombic ZrO2 collapses, and the force becomes too large.
As a result, the other component becomes too small, making it impossible to secure the desired excellent thermal shock resistance.
つきに、この発明のセラミック材料を実施例により（上
体的に説明する。Finally, the ceramic material of the present invention will be explained in detail by way of examples.
実施例
、１Ｌｉｔ＋＝’ｌ粉末として、平均粒径：０６１μｍ
を有する正方晶系ＺｒＯ２粉末、同０．２μｍの斜方晶
系Ｚｒｏ２粉末、同、−＋、 ５ ｐ ｍのＡＭ ２０
、粉末、同０．８μｍのＹ２Ｏ３粉末、同０．３７１
ｍの（フイｇｏ粉末、同０．７ｐｍのＴｉＣ粉末＋
ｂ’１０８ｐ ｍの’Ｉ’ｌＮ粉末、同０．ＢｐｍのＩ
ｌｌ １ｔ：ｏ、、ｌ ｌ ｕ、粉末、同２．０μｍの
Ｎ１粉末、同１．０μｍのＣｏ粉末、同０．９μｍのＭ
ｏ粉末、同０．９μｍのＷ粉末、および同０８μｍのＷ
Ｃ粉末を用意し、これら原料粉末をそれぞれ第１表に示
される配合組成Ｑζ配合し、ボールミルにて４８時時間
式混合し、乾燥し、ついでこの結果の混合粉末に対して
、ポットプレス法（黒鉛型に詰め、温度：１５５０〜１
６ ｂ’ ０ ℃の範囲内の最適温度、圧カニ ２００
ｋｇ／ｆｆｌ、保持時間、１５分の条件で焼結、第１表
にはｒｔ＋どして表示）、あるいは普通焼結法（５に／
／ ｃｉｌの圧力で成形した圧粉体を、真空中、温度
： Ｊ ５５０〜ＩＣ５０℃の範囲内の最適温度に１時
間１′１１持の条件で焼結、第１表には（普）として表
示）を施すことによって、実質的に配合組成と同一の組
成（ただし正方品系ＺｒＯ２と斜方晶系’１ｒ０２との
割合は配置′７状態と焼結状態では変化する）をもった
＋−発明セラミック材料１〜５３および比較セラミック
材ＩＩ １〜１：２をそれぞれ製造した。なお、比較上
”７ミソク材料１〜１２は、いずれも構成成分のうちの
いずれかの成分含有量（第１表に壷印をｆ、ｔ して表
示）がこの発明の範囲から外れた組成をもつも（１）で
ある。Example, 1 Lit+='l powder, average particle size: 061 μm
Tetragonal ZrO2 powder with 0.2 μm orthorhombic Zro2 powder with -+, 5 p m AM 20
, powder, 0.8 μm Y2O3 powder, 0.371
m (figo powder, same 0.7pm TiC powder +
b'I'IN powder of 108 pm, 0. Bpm I
ll 1t:o,, l l u, powder, 2.0 μm N1 powder, 1.0 μm Co powder, 0.9 μm M
o powder, W powder of 0.9 μm, and W powder of 0.8 μm
Prepare C powder, mix these raw material powders with the composition Qζ shown in Table 1, mix in a ball mill for 48 hours, dry, and then apply the pot press method ( Packed into graphite mold, temperature: 1550~1
Optimum temperature within the range of 6 b' 0 °C, pressure crab 200
kg/ffl, holding time, sintering under the conditions of 15 minutes, shown as rt+ in Table 1), or normal sintering method (in 5/
The compacted powder compacted at a pressure of / cil was sintered in vacuum at an optimum temperature within the range of J 550 to IC 50°C for 1 hour at 1'11. ), the +- invention has substantially the same composition as the blended composition (however, the ratio of tetragonal ZrO2 and orthorhombic '1r02 changes between the configuration '7 state and the sintered state). Ceramic Materials 1-53 and Comparative Ceramic Material II 1-1:2 were produced, respectively. For comparison, "7 Misoku Materials 1 to 12" are all compositions in which the content of any one of the constituent components (indicated by the pot marks f and t in Table 1) is outside the scope of this invention. This is also (1).
つきに、この結果得られた本発明セラミック材＊１」〜
Ｓ３および比較セラミック材料１〜１２について、材料
中における正方晶系ＺｒＯ２（第１表にはＩ −２，ｒ
ｌ）２で表小）と斜方晶系ＺｒＯ２（第１表には１・−
Ｚｒ０２で表示）との重量比をＸ＃回折により測定する
と共に、これより研削にて抗折力試験片と、Ｊ１ε・Ｓ
ＮＰ ４３２に則した切削チップを切り出し、抗折力を
測定すると共に、以Ｆの条件、すなわち被剛材：ＦＣ−
３０の角材（硬さ：ＨＨ１８０）。Finally, the ceramic material of the present invention*1 obtained as a result
Regarding S3 and Comparative Ceramic Materials 1 to 12, tetragonal ZrO2 (Table 1 shows I −2, r
l) 2 (table small) and orthorhombic ZrO2 (1・- in Table 1)
Zr02) was measured by X# diffraction, and from this was ground a transverse rupture strength test piece and a J1ε・S
A cutting chip conforming to NP 432 was cut out, the transverse rupture strength was measured, and the following conditions were met: rigid material: FC-
30 square timber (hardness: HH180).
切削速度＝３３０講／１ＩＩ１１．−刀当りの送り：０
２５Ｂ＠ ／ ｒｅｖ、 、切込み：３．Ｏｗｘ、水溶
性切削油剤使用の条件での鋳鉄高速切削試験、並びに被
削材：５ＮＣＮ−８（硬さ：２７０）、切削速度：２５
０ｍ／ａｍ。Cutting speed = 330 courses/1II11. - Feed per sword: 0
25B@/rev, , depth of cut: 3. Owx, cast iron high-speed cutting test under the conditions of using water-soluble cutting fluid, work material: 5NCN-8 (hardness: 270), cutting speed: 25
0m/am.
−刀当りの送り： ０．３５１１／ｒｅｖ、 、切込み
：３ ＩＩ ＋乾式の条件での鋼高速切削試験を行ない
、切刃の逃げ面摩耗が０．３ ｍに至るまでの切削時間
を測定した。これらの測定結果を第１表に合せて示した
。- Feed per knife: 0.3511/rev, Depth of cut: 3 II + A high-speed steel cutting test was conducted under dry conditions, and the cutting time until the flank wear of the cutting edge reached 0.3 m was measured. . These measurement results are also shown in Table 1.
第１表に示される結果から、本発明セラミック材料１〜
５３は、いずれも鋳鉄および鋼の高速切削に際してすぐ
れた切削寿命を示すのに対して。From the results shown in Table 1, it can be seen that ceramic materials 1 to 1 of the present invention
No. 53 exhibited excellent cutting life during high-speed cutting of cast iron and steel.
比較セラミック材料ｌ〜１２においては、材料の特性、
すなわち耐摩耗性、耐熱衝撃性、および高温強度のうち
の少なくともいずれかの特性が劣るなめに満足する切削
性能を示さないことが明らか１′１
である。In comparative ceramic materials 1 to 12, material properties,
In other words, it is clear that the material does not exhibit satisfactory cutting performance due to poor wear resistance, thermal shock resistance, and high-temperature strength.
上述のように、この発明のセラミック材料は、すぐれた
耐摩耗性、耐熱衝撃性、および高温強度を有するので、
これらの特性が要求される鋳鉄および鋼の高速１；ＩＪ
削に切削工員として用いた場合にすぐれた切削性能を発
揮するのである。As mentioned above, the ceramic material of the present invention has excellent wear resistance, thermal shock resistance, and high temperature strength.
High speed 1 of cast iron and steel where these properties are required; IJ
It exhibits excellent cutting performance when used as a cutter for cutting.
Claims (2)
トリウムおよび酸化マグネシウムのうちの１棟または２
種：１〜６％、 炭化チタン、窒化チタン、および炭窒化チタンのうちの
１種または２種以上：３〜３０％、正方晶系酸化ツルコ
ニウムと斜方晶系酸化ツルコニウムおよび不可避不純物
：残り（ただし酸化ジルコニウム；３０％以上含有）、
からなる組成（以上重量％）、並びに少なくとも酸化ノ
ルコニウムが連続相として存在する組織を有し、かつ正
方晶系酸化ツルコニウム／斜方晶系酸化ソ／Ｌコニウム
の重量比： ’、／９〜９／１を満足することを特徴と
する高速切削性能にすぐれた切削工具用セラミック材料
。(1) One or two of aluminum oxide dilO~60%, yttrium oxide and magnesium oxide
Species: 1 to 6%, One or more of titanium carbide, titanium nitride, and titanium carbonitride: 3 to 30%, Tetragonal turconium oxide, orthorhombic turconium oxide, and unavoidable impurities: Remaining ( However, zirconium oxide (containing 30% or more),
(wt%), and a structure in which at least norconium oxide exists as a continuous phase, and the weight ratio of tetragonal turconium oxide/orthorhombic so/Lconium oxide: ', /9 to 9 A ceramic material for cutting tools that has excellent high-speed cutting performance and is characterized by satisfying /1.
リウムおよび酸化マグネシウムのうちのｌ神または２種
：１〜６％、 炭化チタン、窒化チタン、および炭窒化チタンのうちの
１種または２種以上：３〜３０チ、Ｎｉ 、 （＋、、
■Ｃ）、Ｗ、および炭化タングステンのうちのｌ神また
は２種以上：０１〜５％、正方晶系酸化ツルコニウムと
斜方晶系酸化ジルコニウムおよび不可避不純物；残り（
ただし酸化ジルコニウム、３０％以上含有）、からなる
組成（１：１−Ｊ−止針％）、並びに少なくとも酸化ジ
ルコニウムが連続、相どじて存在する組織を有し、かつ
正方晶糸Ｖ（ヒソ及コニウム／斜方晶系酸化ツルコニウ
ムの１１量比 １７９〜９／１を満足することを特徴と
する高速切削性能にすぐれた切削工具用セラミック（１
料。(2) Aluminum oxide: 10 to 60%, one or two of hyttrium oxide and magnesium oxide: 1 to 6%, one or two of titanium carbide, titanium nitride, and titanium carbonitride More than: 3~30chi, Ni, (+,,
■C), W, and tungsten carbide or more: 01-5%, tetragonal turconium oxide, orthorhombic zirconium oxide, and unavoidable impurities; remainder (
However, it has a composition consisting of zirconium oxide (containing 30% or more) (1:1-J-stopping %), and a structure in which at least zirconium oxide exists continuously and one after another, and tetragonal crystal threads V (hysteronium and A ceramic for cutting tools with excellent high-speed cutting performance that satisfies a conium/orthorhombic turconium oxide ratio of 179 to 9/1.
fee.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP57067017A JPS58185477A (en) | 1982-04-21 | 1982-04-21 | High speed cutting ceramic for cutting tool |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP57067017A JPS58185477A (en) | 1982-04-21 | 1982-04-21 | High speed cutting ceramic for cutting tool |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS58185477A true JPS58185477A (en) | 1983-10-29 |
| JPS623795B2 JPS623795B2 (en) | 1987-01-27 |
Family
ID=13332709
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP57067017A Granted JPS58185477A (en) | 1982-04-21 | 1982-04-21 | High speed cutting ceramic for cutting tool |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS58185477A (en) |
Cited By (14)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS60180958A (en) * | 1984-02-27 | 1985-09-14 | 住友電気工業株式会社 | Ceramic sintered body |
| WO1987001980A1 (en) * | 1985-09-27 | 1987-04-09 | Nippon Steel Corporation | Finish cutting tool and finish cutting method for steel |
| JPS62148364A (en) * | 1985-12-23 | 1987-07-02 | 東芝タンガロイ株式会社 | Ceramic elastic member |
| JPS62266158A (en) * | 1986-05-14 | 1987-11-18 | Hitachi Metals Ltd | Doctor blade |
| JPS62277203A (en) * | 1986-05-23 | 1987-12-02 | Kyocera Corp | Cutting tool of aluminum oxide quality |
| JPS6389471A (en) * | 1986-10-03 | 1988-04-20 | 三菱マテリアル株式会社 | Ceramic material for cutting tool |
| JPS6433056A (en) * | 1987-07-27 | 1989-02-02 | Kobe Steel Ltd | Shaft shaped ceramic cutting tool |
| JPH03247555A (en) * | 1990-02-24 | 1991-11-05 | Ssangyong Cement Ind Co Ltd | Manufacture of al3o3-ticx sintered body for cutting rool |
| US5196385A (en) * | 1985-08-06 | 1993-03-23 | Ngk Spark Plug Co., Ltd. | Process for the preparation of a heat-resistant and wear resistant ceramic material |
| US5296008A (en) * | 1991-02-15 | 1994-03-22 | Sumitomo Electric Industries, Ltd. | Method for manufacturing a cutting tool insert made of a silicon nitride body |
| US5525135A (en) * | 1992-10-19 | 1996-06-11 | H. C. Starck Gmbh & Co. Kg | Abrasive material based on zirconium corundum a process for its production and its use |
| CN104131208A (en) * | 2014-08-06 | 2014-11-05 | 南京理工大学 | Aluminium oxide-titanium carbide micron composite ceramic cutter material and microwave sintering method thereof |
| CN105294084A (en) * | 2015-10-10 | 2016-02-03 | 华南理工大学 | High-hardness and high-toughness alumina ceramic composite material and preparing method thereof |
| CN113443912A (en) * | 2020-03-26 | 2021-09-28 | 比亚迪股份有限公司 | Zirconia ceramic and preparation method and application thereof |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5460308A (en) * | 1977-09-14 | 1979-05-15 | Krupp Gmbh | Ceramic formed body for machining metallandd nonmetal processsmaterial* and wearrresisting application* and method of making same |
| JPS5461215A (en) * | 1977-10-05 | 1979-05-17 | Feldmuehle Ag | Sintering material |
-
1982
- 1982-04-21 JP JP57067017A patent/JPS58185477A/en active Granted
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5460308A (en) * | 1977-09-14 | 1979-05-15 | Krupp Gmbh | Ceramic formed body for machining metallandd nonmetal processsmaterial* and wearrresisting application* and method of making same |
| JPS5461215A (en) * | 1977-10-05 | 1979-05-17 | Feldmuehle Ag | Sintering material |
Cited By (18)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS60180958A (en) * | 1984-02-27 | 1985-09-14 | 住友電気工業株式会社 | Ceramic sintered body |
| US5196385A (en) * | 1985-08-06 | 1993-03-23 | Ngk Spark Plug Co., Ltd. | Process for the preparation of a heat-resistant and wear resistant ceramic material |
| WO1987001980A1 (en) * | 1985-09-27 | 1987-04-09 | Nippon Steel Corporation | Finish cutting tool and finish cutting method for steel |
| JPH0818164B1 (en) * | 1985-09-27 | 1996-02-28 | ||
| JPH0469592B2 (en) * | 1985-12-23 | 1992-11-06 | Toshiba Tungaloy Co Ltd | |
| JPS62148364A (en) * | 1985-12-23 | 1987-07-02 | 東芝タンガロイ株式会社 | Ceramic elastic member |
| JPS62266158A (en) * | 1986-05-14 | 1987-11-18 | Hitachi Metals Ltd | Doctor blade |
| JP2564516B2 (en) * | 1986-05-14 | 1996-12-18 | 日立金属株式会社 | Doctor blade |
| JPS62277203A (en) * | 1986-05-23 | 1987-12-02 | Kyocera Corp | Cutting tool of aluminum oxide quality |
| JPS6389471A (en) * | 1986-10-03 | 1988-04-20 | 三菱マテリアル株式会社 | Ceramic material for cutting tool |
| JPH0723263B2 (en) * | 1986-10-03 | 1995-03-15 | 三菱マテリアル株式会社 | Cutting tool made of aluminum oxide based ceramics |
| JPS6433056A (en) * | 1987-07-27 | 1989-02-02 | Kobe Steel Ltd | Shaft shaped ceramic cutting tool |
| JPH03247555A (en) * | 1990-02-24 | 1991-11-05 | Ssangyong Cement Ind Co Ltd | Manufacture of al3o3-ticx sintered body for cutting rool |
| US5296008A (en) * | 1991-02-15 | 1994-03-22 | Sumitomo Electric Industries, Ltd. | Method for manufacturing a cutting tool insert made of a silicon nitride body |
| US5525135A (en) * | 1992-10-19 | 1996-06-11 | H. C. Starck Gmbh & Co. Kg | Abrasive material based on zirconium corundum a process for its production and its use |
| CN104131208A (en) * | 2014-08-06 | 2014-11-05 | 南京理工大学 | Aluminium oxide-titanium carbide micron composite ceramic cutter material and microwave sintering method thereof |
| CN105294084A (en) * | 2015-10-10 | 2016-02-03 | 华南理工大学 | High-hardness and high-toughness alumina ceramic composite material and preparing method thereof |
| CN113443912A (en) * | 2020-03-26 | 2021-09-28 | 比亚迪股份有限公司 | Zirconia ceramic and preparation method and application thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| JPS623795B2 (en) | 1987-01-27 |
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