JP2001322009A - Alumina ceramic cutting tool and manufacturing method therefor - Google Patents
Alumina ceramic cutting tool and manufacturing method thereforInfo
- Publication number
- JP2001322009A JP2001322009A JP2000282215A JP2000282215A JP2001322009A JP 2001322009 A JP2001322009 A JP 2001322009A JP 2000282215 A JP2000282215 A JP 2000282215A JP 2000282215 A JP2000282215 A JP 2000282215A JP 2001322009 A JP2001322009 A JP 2001322009A
- Authority
- JP
- Japan
- Prior art keywords
- alumina
- sintered body
- cutting tool
- cutting
- density
- 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
- PNEYBMLMFCGWSK-UHFFFAOYSA-N Alumina Chemical compound [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 title claims abstract description 99
- 238000005520 cutting process Methods 0.000 title claims abstract description 94
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 24
- 239000000843 powder Substances 0.000 claims abstract description 29
- 238000012545 processing Methods 0.000 claims abstract description 20
- 239000000463 material Substances 0.000 claims abstract description 17
- 229910044991 metal oxide Inorganic materials 0.000 claims abstract description 13
- 239000013078 crystal Substances 0.000 claims abstract description 12
- 238000000034 method Methods 0.000 claims abstract description 12
- 239000002245 particle Substances 0.000 claims description 15
- 150000004706 metal oxides Chemical class 0.000 claims description 12
- 238000005452 bending Methods 0.000 claims description 9
- 239000002994 raw material Substances 0.000 claims description 8
- 238000012360 testing method Methods 0.000 claims description 8
- 229910001018 Cast iron Inorganic materials 0.000 claims description 4
- 238000001513 hot isostatic pressing Methods 0.000 claims description 4
- 238000002156 mixing Methods 0.000 claims description 3
- 239000000203 mixture Substances 0.000 claims 1
- 238000000465 moulding Methods 0.000 claims 1
- 238000005245 sintering Methods 0.000 abstract description 4
- 238000010304 firing Methods 0.000 description 8
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 4
- 150000001875 compounds Chemical class 0.000 description 4
- 239000011148 porous material Substances 0.000 description 3
- 229910052727 yttrium Inorganic materials 0.000 description 3
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 2
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- 238000007545 Vickers hardness test Methods 0.000 description 2
- 229910052769 Ytterbium Inorganic materials 0.000 description 2
- 230000002159 abnormal effect Effects 0.000 description 2
- 239000000919 ceramic Substances 0.000 description 2
- 238000000280 densification Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000011156 evaluation Methods 0.000 description 2
- 230000001747 exhibiting effect Effects 0.000 description 2
- 229910052742 iron Inorganic materials 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 238000013001 point bending Methods 0.000 description 2
- 229910052706 scandium Inorganic materials 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- 238000010998 test method Methods 0.000 description 2
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 2
- 229910018072 Al 2 O 3 Inorganic materials 0.000 description 1
- 238000007088 Archimedes method Methods 0.000 description 1
- 102100036738 Guanine nucleotide-binding protein subunit alpha-11 Human genes 0.000 description 1
- 229910000760 Hardened steel Inorganic materials 0.000 description 1
- 101100283445 Homo sapiens GNA11 gene Proteins 0.000 description 1
- 229910052765 Lutetium Inorganic materials 0.000 description 1
- 229910002651 NO3 Inorganic materials 0.000 description 1
- NHNBFGGVMKEFGY-UHFFFAOYSA-N Nitrate Chemical compound [O-][N+]([O-])=O NHNBFGGVMKEFGY-UHFFFAOYSA-N 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
- 229910010413 TiO 2 Inorganic materials 0.000 description 1
- 238000005299 abrasion Methods 0.000 description 1
- 239000000654 additive Substances 0.000 description 1
- 230000000996 additive effect Effects 0.000 description 1
- 150000004703 alkoxides Chemical class 0.000 description 1
- 229910052786 argon Inorganic materials 0.000 description 1
- 239000012300 argon atmosphere Substances 0.000 description 1
- 239000012298 atmosphere Substances 0.000 description 1
- 239000011230 binding agent Substances 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 229910003460 diamond Inorganic materials 0.000 description 1
- 239000010432 diamond Substances 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 238000005530 etching Methods 0.000 description 1
- 238000000227 grinding Methods 0.000 description 1
- 239000003966 growth inhibitor Substances 0.000 description 1
- 239000012535 impurity Substances 0.000 description 1
- 230000010354 integration Effects 0.000 description 1
- 229910052747 lanthanoid Inorganic materials 0.000 description 1
- 150000002602 lanthanoids Chemical class 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 150000002736 metal compounds Chemical class 0.000 description 1
- 229910052757 nitrogen Inorganic materials 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 238000002360 preparation method Methods 0.000 description 1
- 150000003839 salts Chemical class 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
Landscapes
- Cutting Tools, Boring Holders, And Turrets (AREA)
- Compositions Of Oxide Ceramics (AREA)
Abstract
Description
【０００１】[0001]
【発明の属する技術分野】本発明は、アルミナセラミッ
クス切削工具およびその製造方法に関し、詳しくは、工
具寿命の長いアルミナセラミックス切削工具およびその
製造方法に関する。本発明のアルミナセラミックス切削
工具は、高速切削（例えば切削速度６００〜１０００ｍ
／分）用および難削材切削用の切削工具として特に好適
である。The present invention relates to an alumina ceramic cutting tool and a method for producing the same, and more particularly, to an alumina ceramic cutting tool having a long tool life and a method for producing the same. The alumina ceramic cutting tool of the present invention is capable of high-speed cutting (for example, a cutting speed of 600 to 1000 m).
/ Min) and for cutting difficult-to-cut materials.
【０００２】[0002]
【従来の技術】アルミナ焼結体は高硬度であり、かつ化
学的安定性が高い（鉄との親和性が低い）ため優れた耐
摩耗性を示し、切削工具として鋼、鋳鉄の高速仕上げ加
工等に広く使用されている。しかし、アルミナ焼結体か
らなる工具は強度や靱性が比較的低いため、欠損を起こ
しやすいという問題がある。2. Description of the Related Art Alumina sintered compacts have high hardness and high chemical stability (low affinity with iron), exhibiting excellent wear resistance. High-speed finishing of steel and cast iron as cutting tools Widely used for etc. However, there is a problem that a tool made of an alumina sintered body is liable to be broken due to relatively low strength and toughness.
【０００３】この問題に対し、アルミナ焼結体中にＴｉ
Ｃ粒子を分散させることにより強度、靱性を向上させて
耐欠損性を改善したＡｌ2Ｏ3−ＴｉＣ系材料が知られて
いる（小林正樹、「セラミック工具」、マテリアルイン
テグレーション、13(5),77-85(2000)）。しかし、Ｔｉ
Ｃは耐酸化性、鉄に対する化学的安定性等の点において
アルミナに劣るため、この材料では純アルミナ系材料よ
りも摩耗特性が低下してしまう。一方、純アルミナに粒
成長抑制剤としてＭｇＯを添加し、低温焼成したのち熱
間静水圧プレス処理（以下、ＨＩＰ処理ともいう。）を
行うことにより、組織を微細化し高強度化を図る方法も
提案されている。[0003] In order to solve this problem, Ti is contained in an alumina sintered body.
An Al 2 O 3 —TiC-based material in which the strength and toughness are improved by dispersing C particles to improve fracture resistance is known (Masaki Kobayashi, “Ceramic Tool”, Material Integration, 13 (5), 77-85 (2000)). However, Ti
Since C is inferior to alumina in terms of oxidation resistance, chemical stability against iron, and the like, this material has lower wear characteristics than a pure alumina-based material. On the other hand, there is also a method in which MgO is added to pure alumina as a grain growth inhibitor, calcined at a low temperature, and then subjected to hot isostatic pressing (hereinafter, also referred to as HIP) to thereby refine the structure and increase the strength. Proposed.
【０００４】近年、製造効率の向上等の目的から、従来
（３００ｍ／分程度）より一層の高速切削化の要望がな
されている。このような高速切削では、刃先温度が上昇
するため、切削工具の高温硬度および高温強度の向上が
要求される。また、焼き入れ鋼等の高硬度材（難削材）
の加工においても刃先温度が上昇するため、同様に高温
における硬度および強度が必要である。しかし、従来の
アルミナ系工具は、ＴｉＣやＭｇＯを添加した上記材料
からなるものを含め、高温硬度や高温強度が未だ不十分
である。このため、高速切削（例えば切削速度６００〜
１０００ｍ／分）においては速やかに摩耗またはフレー
キングが生じ、工具寿命が短いという問題がある。[0004] In recent years, there has been a demand for higher speed cutting than in the past (about 300 m / min) for the purpose of improving production efficiency and the like. In such high-speed cutting, since the temperature of the cutting edge increases, the high-temperature hardness and high-temperature strength of the cutting tool are required to be improved. In addition, hardened materials such as hardened steel (difficult-to-cut materials)
Since the temperature of the cutting edge also increases in the processing of (1), hardness and strength at a high temperature are similarly required. However, conventional alumina-based tools, including those made of the above materials to which TiC or MgO is added, still have insufficient high-temperature hardness and high-temperature strength. For this reason, high-speed cutting (for example, a cutting speed of 600 to
(1000 m / min), there is a problem that wear or flaking occurs quickly and the tool life is short.
【０００５】[0005]
【発明が解決しようとする課題】本発明は、上記従来の
問題を解決するものであり、高速切削や高硬度材の切削
に用いられた場合にも長い工具寿命の得られるアルミナ
セラミックス切削工具およびその製造方法を提供するこ
とを目的とする。SUMMARY OF THE INVENTION An object of the present invention is to solve the above-mentioned conventional problems, and to provide an alumina ceramic cutting tool capable of obtaining a long tool life even when used for high-speed cutting or cutting of a hard material. It is an object of the present invention to provide a manufacturing method thereof.
【０００６】[0006]
【課題を解決するための手段】第１発明のアルミナセラ
ミックス切削工具は、３Ａ属金属酸化物から選択される
一種以上の金属酸化物をアルミナ１００モルに対して
０．０２〜２．０モル含み、ＭｇおよびＴｉを含有せ
ず、密度が３．９８ｇ／ｃｍ3以上、アルミナ結晶粒の
平均粒径が０．３〜２．０μｍであるアルミナ焼結体か
らなることを特徴とする。The alumina ceramic cutting tool of the first invention contains at least one metal oxide selected from the group 3A metal oxides in an amount of 0.02 to 2.0 mol per 100 mol of alumina. , Mg and Ti are not contained, and is characterized by comprising an alumina sintered body having a density of 3.98 g / cm 3 or more and an average grain size of alumina crystal grains of 0.3 to 2.0 μm.
【０００７】上記３Ａ族金属酸化物における「３Ａ族金
属」としては、Ｓｃ、Ｙおよびランタノイドが好ましく
用いられ、このうちＳｃ、Ｙ、Ｌａ、Ｄｙ、Ｙｂ、Ｌｕ
がより好ましく、ＹおよびＹｂが特に好ましく、Ｙｂが
最も好ましい。この３Ａ族金属酸化物の含有量は、アル
ミナ１００モルに対して０．０２〜２．０モル（好まし
くは０．０５〜０．２モル）の範囲とする。この含有量
が０．０２モル未満では高温における強度または硬度が
不足する。一方、含有量が２．０ｍｏｌ％を超えるとこ
れらの酸化物自身、これらの酸化物とアルミナとの化合
物、もしくはその両方が粒界に偏析して、室温および高
温における焼結体の強度および硬度が低下する。また、
焼結体の原材料費を抑えるためには含有量を０．２ｍｏ
ｌ％以下とすることが好ましい。As the “group 3A metal” in the above group 3A metal oxide, Sc, Y and lanthanoids are preferably used. Among them, Sc, Y, La, Dy, Yb, Lu
Is more preferable, Y and Yb are particularly preferable, and Yb is most preferable. The content of the Group 3A metal oxide is in the range of 0.02 to 2.0 mol (preferably 0.05 to 0.2 mol) per 100 mol of alumina. If the content is less than 0.02 mol, the strength or hardness at high temperature is insufficient. On the other hand, if the content exceeds 2.0 mol%, these oxides themselves, a compound of these oxides and alumina, or both of them segregate at the grain boundaries, and the strength and hardness of the sintered body at room temperature and high temperature Decrease. Also,
In order to reduce the raw material cost of the sintered body, the content should be 0.2mo
It is preferably set to 1% or less.
【０００８】上記アルミナ焼結体はＭｇ（例えばＭｇ
Ｏ）およびＴｉ（例えばＴｉＣ、ＴｉＯ2）を「含有し
ない」ことを特徴とする。アルミナ中にこれらの元素ま
たは化合物を含有させると、室温における硬度および強
度については向上がみられる場合もあるが、高温におけ
る硬度および強度はむしろ低下する。また、これらの元
素または化合物と３Ａ族金属酸化物とを併用した場合に
は、３Ａ族金属酸化物の添加による効果を相殺してしま
う恐れがある。The alumina sintered body is made of Mg (eg, Mg
O) and Ti (eg, TiC, TiO 2 ). When these elements or compounds are contained in alumina, the hardness and strength at room temperature may be improved, but the hardness and strength at high temperatures are rather reduced. When these elements or compounds are used in combination with a Group 3A metal oxide, the effect of the addition of the Group 3A metal oxide may be offset.
【０００９】アルミナ焼結体を構成する上記アルミナ結
晶粒の平均粒径は０．３〜２．０μｍの範囲である。ア
ルミナ結晶粒の平均粒径が２．０μｍを超える場合は、
室温および高温における焼結体の強度や硬度が小さくな
り、この焼結体からなる切削工具の切削性能が低下す
る。一方、アルミナ結晶粒の平均粒径が０．３μｍ未満
であるアルミナ焼結体は、安価な原料粉末を用いて（例
えば、焼成−ＨＩＰ処理といった量産手法により）生成
させることが難しく、得られる焼結体がコスト高にな
る。また、粒径が小さすぎるため３Ａ属金属酸化物の添
加効果が現れず、高温における硬度および強度が不足す
るので、この焼結体を用いた切削工具は高速切削や高硬
度材切削における切削性能が不十分なものとなる。The average grain size of the alumina crystal grains constituting the alumina sintered body is in the range of 0.3 to 2.0 μm. When the average particle size of the alumina crystal grains exceeds 2.0 μm,
The strength and hardness of the sintered body at room temperature and high temperature are reduced, and the cutting performance of a cutting tool made of the sintered body is reduced. On the other hand, it is difficult to produce an alumina sintered body having an average particle diameter of alumina crystal grains of less than 0.3 μm using inexpensive raw material powder (for example, by a mass production method such as sintering-HIP treatment). The union becomes expensive. In addition, since the particle size is too small, the effect of adding the Group 3A metal oxide does not appear, and the hardness and strength at high temperatures are insufficient. Therefore, the cutting tool using this sintered body has high cutting performance in high-speed cutting and high-hardness material cutting. Is inadequate.
【００１０】また、アルミナ焼結体を構成するアルミナ
結晶粒の平均粒径が大きくなるにつれて、この焼結体を
切削工具形状に加工する際の加工性が向上するため加工
コストが低減する。高速切削および高硬度材切削におけ
る十分な切削性能を維持しつつ実用的な加工性を得るた
めには、アルミナ結晶粒の平均粒径が０．５〜１．７μ
ｍであることが好ましく、０．８〜１．５μｍであるこ
とが特に好ましい。なお、より加工性を重視する場合に
は、アルミナ結晶粒の平均粒径を、１．０μｍを超えて
１．７μｍ以下の範囲とすることもできる。[0010] Further, as the average grain size of the alumina crystal grains constituting the alumina sintered body increases, the workability in processing the sintered body into a cutting tool shape is improved, so that the processing cost is reduced. In order to obtain practical workability while maintaining sufficient cutting performance in high-speed cutting and high-hardness material cutting, the average grain size of alumina crystal grains is 0.5 to 1.7 μm.
m, particularly preferably 0.8 to 1.5 μm. In the case where emphasis is placed on workability, the average grain size of the alumina crystal grains may be set to a range exceeding 1.0 μm and not more than 1.7 μm.
【００１１】上記アルミナ焼結体の密度は３．９８ｇ／
ｃｍ3以上であり、特に３．９９ｇ／ｃｍ3以上（上限は
このアルミナ焼結体の理論密度である。）であることが
好ましい。アルミナ焼結体の密度が３．９８ｇ／ｃｍ3
未満である場合は、焼結体の緻密化が不十分となり、室
温および高温における強度や硬度が小さくなって、この
焼結体からなる切削工具の切削性能が低下する。The density of the alumina sintered body is 3.98 g /
cm 3 or more, and particularly preferably 3.99 g / cm 3 or more (the upper limit is the theoretical density of the alumina sintered body). The density of the alumina sintered body is 3.98 g / cm 3
If it is less than 1, the densification of the sintered body is insufficient, the strength and hardness at room temperature and high temperature are reduced, and the cutting performance of the cutting tool made of the sintered body is reduced.
【００１２】第１発明の切削工具におけるアルミナ焼結
体は、第２発明のように、室温における曲げ強度および
ビッカース硬度がそれぞれ７００ＭＰａ以上（好ましく
は７５０ＭＰａ以上、上限は特に限定されないが通常は
９００〜１０００ＭＰａ程度）および１８００以上（好
ましくは１９００以上、上限は特に限定されないが通常
は２１００〜２２００程度）、１０００℃における曲げ
強度およびビッカース硬度がそれぞれ５００ＭＰａ以上
（好ましくは５５０ＭＰａ以上、上限は特に限定されな
いが通常は６５０ＭＰａ程度）および７００以上（好ま
しくは８００以上、上限は特に限定されないが通常は１
０００程度）、かつ１２００℃における曲げ強度が４０
０ＭＰａ以上（好ましくは４５０ＭＰａ以上、上限は特
に限定されないが通常は６００ＭＰａ程度）であるもの
とすることができる。第２発明の切削工具は、室温から
高温までの温度範囲において所定の高い硬度および強度
を示すアルミナ焼結体からなるので、さらに高速切削性
および高硬度材切削性に優れる。The alumina sintered body in the cutting tool of the first invention has a bending strength and a Vickers hardness at room temperature of 700 MPa or more (preferably 750 MPa or more, and the upper limit is not particularly limited, but is usually 900 to 900, as in the second invention). The bending strength and the Vickers hardness at 1000 ° C. are 500 MPa or more (preferably 550 MPa or more, and the upper limit is not particularly limited). Usually, about 650 MPa) and 700 or more (preferably 800 or more, the upper limit is not particularly limited, but usually 1
2,000) and a bending strength at 1200 ° C. of 40
It can be 0 MPa or more (preferably 450 MPa or more, and the upper limit is not particularly limited, but is usually about 600 MPa). Since the cutting tool of the second invention is made of an alumina sintered body having a predetermined high hardness and strength in a temperature range from room temperature to a high temperature, the cutting tool is further excellent in high-speed cutting property and high-hardness material cutting property.
【００１３】第１発明または第２発明の切削工具は、第
３発明のように、下記条件で切削試験を行った場合にお
いて、切削可能な距離が７００ｍ以上（好ましくは７５
０ｍ以上）であるものとすることができる。 〔切削試験条件〕 工具形状；ＳＮＧＮ４３４ 被削材；鋳鉄 切削条件；ドライ 切削速度Ｖ＝１０００ｍ／分 工具送りｆ＝０．３０ｍｍ／ｒｅｖ 切削深さｄ＝２．０ｍｍThe cutting tool of the first invention or the second invention has a cutting distance of 700 m or more (preferably 75 m) when a cutting test is performed under the following conditions as in the third invention.
0 m or more). [Cutting test conditions] Tool shape: SNGN434 Work material: Cast iron Cutting conditions: Dry Cutting speed V = 1000 m / min Tool feed f = 0.30 mm / rev Cutting depth d = 2.0 mm
【００１４】第４発明、第５発明および第６発明は、第
１発明から第３発明のアルミナセラミックス切削工具を
製造する方法に関する。すなわち、第４発明の製造方法
は、平均粒径が２．０μｍ以下であり純度が９９．９９
％以上であるアルミナ粉末を他の原料粉末と混合して所
定形状に成形した後、焼成して３．７７〜３．９１ｇ／
ｃｍ3（より好ましくは３．８０〜３．８８ｇ／ｃｍ3）
の密度を有する一次焼結体とし、次いで、該一次焼結体
にＨＩＰ処理を施して３．９８ｇ／ｃｍ3以上（より好
ましくは３．９９ｇ／ｃｍ3以上）の密度を有する二次
焼結体とすることにより上記アルミナ焼結体を製造し、
その後、該アルミナ焼結体を切削工具形状に加工するこ
とを特徴とする。The fourth, fifth and sixth inventions relate to a method for producing the alumina ceramic cutting tool of the first to third inventions. That is, in the production method of the fourth invention, the average particle size is 2.0 μm or less and the purity is 99.99.
% Or more of alumina powder is mixed with other raw material powders, molded into a predetermined shape, and then calcined to obtain 3.77 to 3.91 g /
cm 3 (more preferably 3.80 to 3.88 g / cm 3 )
Secondary sintered body having a density of 3.98 g / cm 3 or more (more preferably 3.99 g / cm 3 or more) by subjecting the primary sintered body to HIP treatment. By producing the alumina sintered body by making a body,
Thereafter, the alumina sintered body is processed into a cutting tool shape.
【００１５】また、第５発明の製造方法は、平均粒径が
２．０μｍ以下であり純度が９９．９９％以上であるア
ルミナ粉末を他の原料粉末と混合して所定形状に成形し
た後、焼成して理論密度に対する相対密度が９４．５〜
９８．０％（より好ましくは９６．５〜９８．０％）で
ある一次焼結体とし、次いで、該一次焼結体にＨＩＰ処
理を施して理論密度に対する相対密度が９９．８％以上
（より好ましくは９９．９％以上）の二次焼結体とする
ことにより上記アルミナ焼結体を製造し、その後、該ア
ルミナ焼結体を切削工具形状に加工することを特徴とす
る。[0015] Further, according to the production method of the fifth invention, the alumina powder having an average particle size of 2.0 μm or less and a purity of 99.99% or more is mixed with other raw material powders and formed into a predetermined shape. After firing, the relative density with respect to the theoretical density is 94.5 to
A primary sintered body of 98.0% (more preferably 96.5 to 98.0%) is formed, and then the primary sintered body is subjected to HIP treatment to have a relative density with respect to the theoretical density of 99.8% or more ( (More preferably 99.9% or more) to produce the above-mentioned alumina sintered body by forming a secondary sintered body, and thereafter, processing the alumina sintered body into a cutting tool shape.
【００１６】そして、第６発明の製造方法は、平均粒径
が２．０μｍ以下であり純度が９９．９９％以上である
アルミナ粉末を所定形状に成形した後、１２７０〜１３
６０℃（より好ましくは１２８０〜１３４０℃）で焼成
して一次焼結体とし、次いで、該一次焼結体に温度１２
５０〜１５００℃（より好ましくは１３００〜１４００
℃）、圧力５００〜２０００ｋｇ／ｃｍ2（より好まし
くは１０００〜２０００ｋｇ／ｃｍ2）のＨＩＰ処理を
施して二次焼結体とすることにより上記アルミナ焼結体
を製造し、その後、該アルミナ焼結体を切削工具形状に
加工することを特徴とする。The manufacturing method according to the sixth aspect of the present invention is characterized in that, after forming an alumina powder having an average particle size of 2.0 μm or less and a purity of 99.99% or more into a predetermined shape, 1270 to 13
It is baked at 60 ° C. (more preferably 1280 to 1340 ° C.) to obtain a primary sintered body.
50 to 1500 ° C. (more preferably 1300 to 1400
C) and a pressure of 500 to 2000 kg / cm 2 (more preferably 1000 to 2000 kg / cm 2 ) to produce a secondary sintered body, thereby producing the alumina sintered body. It is characterized in that the union is processed into a cutting tool shape.
【００１７】第４発明の製造方法において、一次焼結体
の密度が３．９１ｇ／ｃｍ3よりも高くなるような条件
でこの一次焼結体を焼成するとアルミナの粒成長が起こ
り、目的とする切削性能を備えた工具を得ることが困難
となる。一方、一次焼結体の密度が３．７７ｇ／ｃｍ3
未満では、後のＨＩＰ処理においてこの一次焼結体を十
分に緻密化できず、密度３．９８ｇ／ｃｍ3以上のアル
ミナ焼結体が得られない場合がある。In the manufacturing method of the fourth invention, when the primary sintered body is fired under the condition that the density of the primary sintered body is higher than 3.91 g / cm 3 , alumina grain growth occurs, and the intended purpose is obtained. It becomes difficult to obtain a tool having cutting performance. On the other hand, the density of the primary sintered body is 3.77 g / cm 3.
If it is less than 3, the primary sintered body cannot be sufficiently densified in the subsequent HIP treatment, and an alumina sintered body having a density of 3.98 g / cm 3 or more may not be obtained.
【００１８】また、第５発明の製造方法において、一次
焼結体の理論密度に対する相対密度が９８．０％を超え
るような条件でこの一次焼結体を焼成すると、アルミナ
の粒成長や異常粒成長が起こり易くなり、目的とする切
削性能を備えた工具を得ることが困難となる。一方、一
次焼結体の相対密度が９６．５％未満では、後のＨＩＰ
処理においてこの一次焼結体を十分に緻密化できず、密
度３．９８ｇ／ｃｍ3以上の二次焼結体（本発明のアル
ミナ焼結体）が得られない場合がある。In the manufacturing method according to the fifth aspect of the present invention, when the primary sintered body is fired under the condition that the relative density with respect to the theoretical density of the primary sintered body exceeds 98.0%, grain growth of alumina and abnormal grain size are caused. Growth tends to occur, and it is difficult to obtain a tool having the intended cutting performance. On the other hand, if the relative density of the primary sintered body is less than 96.5%, the subsequent HIP
In the treatment, the primary sintered body may not be sufficiently densified, and a secondary sintered body (alumina sintered body of the present invention) having a density of 3.98 g / cm 3 or more may not be obtained.
【００１９】第６発明の製造方法において焼成温度を１
２７０〜１３６０℃とするのは、上記密度および／また
は理論密度の一次焼結体を得やすいためである。焼成温
度が１３６０℃を超えるとアルミナの粒成長が起こり、
目的とする切削性能を備えた工具を得ることが困難とな
る。一方、焼成温度が１２７０℃未満では、密度３．７
７ｇ／ｃｍ3以上の一次焼結体を得ることは困難であ
る。また、ＨＩＰ処理温度を１２５０〜１５００℃、処
理圧力を５００〜２０００ｋｇ／ｃｍ2とするのは、温
度が上記範囲を超えるとアルミナの粒成長や異常粒成長
が起こり易くなり、強度、硬度および耐摩耗性の低下を
招くためである。一方、温度および／または圧力が上記
範囲未満では密度３．９８ｇ／ｃｍ3以上のアルミナ焼
結体を得ることが困難である。なお、ＨＩＰ処理の圧力
は、２０００ｋｇ／ｃｍ2を超える場合も切削性能に優
れた切削工具を製造することはできるが、得られる切削
工具がコスト高となるため２０００ｋｇ／ｃｍ2の処理
圧力とすることが好ましい。このＨＩＰ処理は窒素、ア
ルゴン等の不活性雰囲気において行うことができ、処理
温度および圧力を保持する時間は例えば０．５〜３時
間、好ましくは１〜２時間程度である。In the manufacturing method of the sixth invention, the firing temperature is set to 1
The reason for setting the temperature to 270 to 1360 ° C. is to easily obtain a primary sintered body having the above density and / or theoretical density. If the firing temperature exceeds 1360 ° C., alumina grain growth occurs,
It becomes difficult to obtain a tool having the desired cutting performance. On the other hand, when the firing temperature is lower than 1270 ° C., the density is 3.7.
It is difficult to obtain a primary sintered body of 7 g / cm 3 or more. Further, the reason why the HIP processing temperature is set to 1250 to 1500 ° C. and the processing pressure is set to 500 to 2000 kg / cm 2 is that if the temperature exceeds the above range, alumina grain growth or abnormal grain growth is likely to occur, and strength, hardness and resistance to heat are increased. This is because the wear property is reduced. On the other hand, if the temperature and / or pressure is less than the above range, it is difficult to obtain an alumina sintered body having a density of 3.98 g / cm 3 or more. When the pressure of the HIP processing is more than 2000 kg / cm 2 , a cutting tool having excellent cutting performance can be manufactured. However, since the obtained cutting tool is expensive, the processing pressure is set to 2000 kg / cm 2. Is preferred. This HIP processing can be performed in an inert atmosphere such as nitrogen or argon, and the time for maintaining the processing temperature and pressure is, for example, about 0.5 to 3 hours, preferably about 1 to 2 hours.
【００２０】第４〜第６発明の製造方法において、アル
ミナ粉末とともに成形される「他の原料粉末」として
は、３Ａ族金属酸化物の粉末を用いてもよく、また加熱
等により焼結後に３Ａ族金属酸化物となる化合物（例え
ば金属アルコキシド等の有機金属化合物、硝酸塩等の塩
類）の粉末を用いてもよく、これらを併用してもよい。In the manufacturing method of the fourth to sixth inventions, as the "other raw material powder" molded together with the alumina powder, a powder of a 3A metal oxide may be used. A powder of a compound (for example, an organic metal compound such as a metal alkoxide, or a salt such as a nitrate) which becomes a group metal oxide may be used, or may be used in combination.
【００２１】焼結体の製造に用いる上記アルミナ粉末の
平均粒径は２．０μｍ以下であり、０．２〜１．０μｍ
であることが好ましい。この平均粒径が２．０μｍを超
える場合は、得られる焼結体の強度および硬度が小さく
なり、耐摩耗性等も低下するため、所望の性能を備えた
切削工具を得ることが困難となる。なお、平均粒径が
０．２μｍ未満のアルミナ粉末を用いた場合にも切削性
能に優れた切削工具を製造することはできるが、そのよ
うな微粉末は高価であるため、平均粒径０．２μｍ以上
の粉末を用いることが好ましい。The average particle size of the alumina powder used for producing the sintered body is 2.0 μm or less, and 0.2 to 1.0 μm
It is preferred that When the average particle size exceeds 2.0 μm, the strength and hardness of the obtained sintered body decrease, and the wear resistance and the like also decrease, so that it is difficult to obtain a cutting tool having desired performance. . A cutting tool having excellent cutting performance can be produced even when alumina powder having an average particle size of less than 0.2 μm is used. It is preferable to use a powder of 2 μm or more.
【００２２】本発明の製造方法によると、後のＨＩＰ処
理により所定以上の緻密化が可能な範囲で、一次焼結体
の密度を（例えば一次焼結体を低温で焼成する等の方法
で）低く抑えることにより、粒成長を抑制するととも
に、残留気孔が小さくしかも粒界にのみ分布した一次焼
結体を作製することができる。このような一次焼結体を
ＨＩＰ処理することによって残留気孔が容易に排出(消
失)され、その結果として、焼結体の残留気孔がほぼ完
全に消失した高密度のアルミナ焼結体からなるアルミナ
セラミックス切削工具を作製することができる。また、
３Ａ族金属酸化物を添加することにより高温における強
度および硬度が向上する理由は必ずしも明らかではない
が、おそらくこれらの酸化物は粒界に沿って極薄く偏析
し、粒界の結合力を高め、かつ／または拡散を抑制して
いるものと考えられる。According to the manufacturing method of the present invention, the density of the primary sintered body is reduced (for example, by sintering the primary sintered body at a low temperature) within a range where densification of a predetermined level or more can be performed by the subsequent HIP treatment. By suppressing the grain size to a low level, it is possible to suppress the grain growth and produce a primary sintered body having small residual pores and distributed only at the grain boundaries. By subjecting such a primary sintered body to HIP treatment, residual pores are easily discharged (disappeared), and as a result, an alumina composed of a high-density alumina sintered body in which residual pores of the sintered body are almost completely eliminated. A ceramic cutting tool can be manufactured. Also,
It is not clear why the addition of Group 3A metal oxides increases the strength and hardness at high temperatures, but probably these oxides segregate very thinly along the grain boundaries, increasing the bonding strength of the grain boundaries, And / or it is considered that diffusion is suppressed.
【００２３】[0023]
【発明の実施の形態】以下、実施例によって本発明を更
に詳しく説明する。 （１）アルミナ焼結体の作製 平均粒径０．２μｍ、純度９９．９９％以上のアルミナ
粉末と、このアルミナ粉末１００モルに対して表１に示
す添加物量に相当する他の原料粉末とを、高純度アルミ
ナ球石（純度９９．５％以上）を使用し、水を媒体とし
て湿式混合した。なお、球石としてアルミナ純度９９．
５％以上のものを用いたので、球石の摩耗による不純物
の混入を低減できる。必要に応じてバインダを添加して
噴霧乾燥した後、所定形状に成形し、この成形体を表１
に記載の温度で焼成し、次いで、この一次焼結体に対し
て表１に記載の温度および圧力でＨＩＰ処理を施した。
このとき、すべての試料において焼成は大気中で行い、
焼成温度での保持時間は２時間とした。また、ＨＩＰ処
理はアルゴン雰囲気で行い、ＨＩＰ処理温度および圧力
での保持時間は１時間とした。DESCRIPTION OF THE PREFERRED EMBODIMENTS Hereinafter, the present invention will be described in more detail by way of examples. (1) Preparation of Alumina Sintered Body An alumina powder having an average particle size of 0.2 μm and a purity of 99.99% or more, and another raw material powder corresponding to the additive amount shown in Table 1 with respect to 100 moles of the alumina powder And high-purity alumina cobblestone (purity of 99.5% or more) was wet-mixed using water as a medium. In addition, alumina purity 99.
Since 5% or more is used, mixing of impurities due to wear of the cobblestone can be reduced. If necessary, a binder is added and spray-dried, and then molded into a predetermined shape.
Then, the primary sintered body was subjected to a HIP treatment at the temperature and pressure shown in Table 1 below.
At this time, firing was performed in air for all samples,
The holding time at the firing temperature was 2 hours. The HIP processing was performed in an argon atmosphere, and the holding time at the HIP processing temperature and pressure was set to 1 hour.
【００２４】（２）アルミナ焼結体の評価 得られたアルミナ焼結体について、焼成後の一次焼結体
の密度（「一次密度」ともいう。）、ＨＩＰ処理後の二
次焼結体の密度（「ＨＩＰ処理後密度」ともいう。）を
測定した。その結果を表１に示す。また、得られたアル
ミナ焼結体につき、アルミナ結晶粒の平均粒径、室温お
よび高温における曲げ強度とビッカース硬度を下記の方
法によって測定した。その結果を表２に示す。(2) Evaluation of Alumina Sintered Body Regarding the obtained alumina sintered body, the density of the primary sintered body after firing (also referred to as “primary density”) and the secondary sintered body after HIP processing The density (also referred to as “density after HIP processing”) was measured. Table 1 shows the results. The average particle size of alumina crystal grains, bending strength at room temperature and high temperature, and Vickers hardness of the obtained alumina sintered body were measured by the following methods. Table 2 shows the results.
【００２５】各測定は以下の方法により行った。 焼成後の一次密度およびＨＩＰ処理後密度；ＪＩＳ
Ｒ １６３４に定められたアルキメデス法により測定し
た（数値はＪＩＳ Ｚ ８４０１に従って小数点以下２
けたに丸めた。）。 アルミナ結晶粒の平均粒径；焼結体を鏡面研磨し、サ
ーマルエッチングした後、走査型電子顕微鏡（ＳＥＭ）
写真を撮り、このＳＥＭ写真からインターセプト法によ
り算出した。Each measurement was performed by the following method. Primary density after firing and density after HIP treatment; JIS
R 1634 was measured by the Archimedes method (the numerical values are 2 decimal places according to JIS Z8401).
Rounded to the right. ). Average grain size of alumina crystal grains; mirror-polished sintered body and thermal etching, then scanning electron microscope (SEM)
A photograph was taken and calculated from the SEM photograph by the intercept method.
【００２６】アルミナ焼結体の室温曲げ強度；ＪＩＳ
Ｒ １６０１に定められた曲げ強さ試験方法により、
室温における３点曲げ強度を測定した。 アルミナ焼結体の高温曲げ強度；ＪＩＳ Ｒ １６０
４に定められた曲げ強さ試験方法により、１０００℃お
よび１２００℃における３点曲げ強度を測定した。 アルミナ焼結体の室温硬度；ＪＩＳ Ｒ １６１０に
定められたビッカース硬さ試験方法により、荷重１ｋｇ
ｆ（９．８０７Ｎ）で測定した。 アルミナ焼結体の高温硬度；ＪＩＳ Ｒ １６２３に
定められたビッカース硬さ試験方法により、荷重１ｋｇ
ｆ（９．８０７Ｎ）で測定した。Room temperature bending strength of alumina sintered body: JIS
According to the bending strength test method defined in R 1601,
The three-point bending strength at room temperature was measured. High temperature bending strength of alumina sintered body; JIS R 160
The three-point bending strength at 1000 ° C. and 1200 ° C. was measured by the bending strength test method specified in No. 4. Room temperature hardness of alumina sintered body; load 1 kg according to Vickers hardness test method specified in JIS R 1610
f (9.807 N). High-temperature hardness of alumina sintered body; load 1 kg according to Vickers hardness test method specified in JIS R 1623
f (9.807 N).
【００２７】（３）アルミナセラミックス切削工具の評
価 得られた焼結体をＳＮＧＮ４３４形状に加工し、以下の
条件で切削試験を行った。試験は各試料につき３回ずつ
行い、フレーキングに至るまでの切削距離の平均値を求
めた。その結果を表２に示す。 〔切削試験条件〕 工具形状；ＳＮＧＮ４３４ 被削材；鋳鉄 切削条件；ドライ 切削速度Ｖ＝１０００ｍ／分 工具送りｆ＝０．３０ｍｍ／ｒｅｖ 切削深さｄ＝２．０ｍｍ(3) Evaluation of Alumina Ceramic Cutting Tool The obtained sintered body was processed into an SNGN434 shape, and a cutting test was performed under the following conditions. The test was performed three times for each sample, and the average value of the cutting distance until flaking was determined. Table 2 shows the results. [Cutting test conditions] Tool shape: SNGN434 Work material: Cast iron Cutting conditions: Dry Cutting speed V = 1000 m / min Tool feed f = 0.30 mm / rev Cutting depth d = 2.0 mm
【００２８】また、試料No.１〜６および１０、１４、
１５の焼結体については、工具形状への加工性の指標と
して、次の方法により研削性を評価した。すなわち、試
料を４５μｍダイヤモンドホイール（ＳＤ Ｄ４５ Ｊ
１００Ｂ）に面圧１ｋｇ／ｃｍ2にて５分間押しつ
け、このときの摩耗量（摩耗深さ）を測定した。なお、
試験は湿式（水）にて行い、試料断面積は１３ｍｍ×１
３ｍｍで統一した。摩耗量は１分間当たりに研削される
体積量に換算した。その結果を表２に示す。Samples Nos. 1 to 6 and 10, 14,
About 15 sintered bodies, grindability was evaluated by the following method as an index of workability into a tool shape. That is, a sample was placed on a 45 μm diamond wheel (SD D45J).
100B) at a surface pressure of 1 kg / cm 2 for 5 minutes, and the amount of wear (wear depth) at this time was measured. In addition,
The test was carried out by a wet method (water), and the sample cross-sectional area was
It was unified at 3 mm. The amount of abrasion was converted to the volume of grinding per minute. Table 2 shows the results.
【００２９】[0029]
【表１】 [Table 1]
【００３０】[0030]
【表２】 [Table 2]
【００３１】表２から判るように、本発明のアルミナセ
ラミックス切削工具はいずれも室温および高温での強
度、硬度に優れた焼結体からなるので、１０００ｍ／分
という高速切削においても７００ｍ以上の切削が可能で
あり、工具寿命の長いものであった。また、アルミナ結
晶粒の粒径が大きくなるにつれて研削性（加工性）は向
上する。例えば試料No.４〜６の焼結体は、比較例の試
料No.１４および１５と同等以上の加工性を示しなが
ら、これらの試料よりも高温硬度が高いため、高速切削
における寿命が長く良好な切削工具とすることができ
た。As can be seen from Table 2, the alumina ceramic cutting tool of the present invention is made of a sintered body having excellent strength and hardness at room temperature and high temperature. Was possible, and the tool life was long. Further, as the grain size of the alumina crystal grains increases, the grindability (workability) improves. For example, the sintered bodies of Samples Nos. 4 to 6 have higher hot hardness than these samples while exhibiting workability equal to or higher than that of Samples Nos. 14 and 15 of Comparative Example, and thus have a long life in high-speed cutting and are good. Cutting tool.
【００３２】[0032]
【発明の効果】本発明のアルミナセラミックス切削工具
は、室温および高温における強度、硬度に優れたアルミ
ナ焼結体から形成されているので、高速切削あるいは難
削材の切削用においても優れた切削性を示す（例えば工
具寿命が長い）。この切削工具は、本発明の製造方法に
より好適に製造することができる。Since the alumina ceramic cutting tool of the present invention is formed of an alumina sintered body having excellent strength and hardness at room temperature and high temperature, it has excellent machinability even for high-speed cutting or for cutting difficult-to-cut materials. (For example, the tool life is long). This cutting tool can be suitably manufactured by the manufacturing method of the present invention.
フロントページの続き (72)発明者 飯尾 聡 名古屋市瑞穂区高辻町14番18号 日本特殊 陶業株式会社内 Ｆターム(参考） 3C046 FF33 FF57 4G030 AA11 AA12 AA36 BA19 GA09 GA11 Continuation of the front page (72) Inventor Satoshi Iio 14-18 Takatsuji-cho, Mizuho-ku, Nagoya F-term (reference) in Japan Special Ceramics Co., Ltd. 3C046 FF33 FF57 4G030 AA11 AA12 AA36 BA19 GA09 GA11
Claims (6)
上の金属酸化物をアルミナ１００モルに対して０．０２
〜２．０モル含み、ＭｇおよびＴｉを含有せず、密度が
３．９８ｇ／ｃｍ3以上、アルミナ結晶粒の平均粒径が
０．３〜２．０μｍであるアルミナ焼結体からなること
を特徴とするアルミナセラミックス切削工具。1. One or more metal oxides selected from Group 3A metal oxides are added in an amount of 0.02 to 100 moles of alumina.
The alumina sintered body contains no more than 2.0 mol, does not contain Mg and Ti, has a density of 3.98 g / cm 3 or more, and has an average grain size of alumina crystal grains of 0.3 to 2.0 μm. Characterized alumina ceramic cutting tool.
げ強度およびビッカース硬度がそれぞれ７００ＭＰａ以
上および１８００以上であり、１０００℃における曲げ
強度およびビッカース硬度がそれぞれ５００ＭＰａ以上
および７００以上であり、かつ１２００℃における曲げ
強度が４００ＭＰａ以上である請求項１記載のアルミナ
セラミックス切削工具。2. The alumina sintered body has a flexural strength and a Vickers hardness at room temperature of 700 MPa or more and 1800 or more, respectively, a flexural strength and a Vickers hardness at 1000 ° C. of 500 MPa or more and 700 or more, and 1200 ° C. 2. The alumina ceramic cutting tool according to claim 1, wherein the bending strength is 400 MPa or more.
て、切削可能な距離が７００ｍ以上である請求項１また
は２記載のアルミナセラミックス切削工具。 〔切削試験条件〕 工具形状；ＳＮＧＮ４３４ 被削材；鋳鉄 切削条件；ドライ 切削速度Ｖ＝１０００ｍ／分 工具送りｆ＝０．３０ｍｍ／ｒｅｖ 切削深さｄ＝２．０ｍｍ3. The alumina ceramic cutting tool according to claim 1, wherein a cutting distance is 700 m or more when a cutting test is performed under the following conditions. [Cutting test conditions] Tool shape: SNGN434 Work material: Cast iron Cutting conditions: Dry Cutting speed V = 1000 m / min Tool feed f = 0.30 mm / rev Cutting depth d = 2.0 mm
ルミナセラミックス切削工具の製造方法であって、 平均粒径が２．０μｍ以下であり純度が９９．９９％以
上であるアルミナ粉末を他の原料粉末と混合して所定形
状に成形した後、焼成して３．７７〜３．９１ｇ／ｃｍ
3の密度を有する一次焼結体とし、次いで、該一次焼結
体に熱間静水圧プレス処理を施して３．９８ｇ／ｃｍ3
以上の密度を有する二次焼結体とすることにより上記ア
ルミナ焼結体を製造し、その後、該アルミナ焼結体を切
削工具形状に加工することを特徴とするアルミナセラミ
ックス切削工具の製造方法。4. The method for producing an alumina ceramic cutting tool according to claim 1, wherein the alumina powder has an average particle size of 2.0 μm or less and a purity of 99.99% or more. After mixing with other raw material powders and forming into a predetermined shape, it is baked to obtain 3.77 to 3.91 g / cm.
3. A primary sintered body having a density of 3. Then, the primary sintered body was subjected to hot isostatic pressing to give 3.98 g / cm 3
A method for manufacturing an alumina ceramic cutting tool, comprising manufacturing the alumina sintered body by forming a secondary sintered body having the above density, and then processing the alumina sintered body into a cutting tool shape.
ルミナセラミックス切削工具の製造方法であって、 平均粒径が２．０μｍ以下であり純度が９９．９９％以
上であるアルミナ粉末を他の原料粉末と混合して所定形
状に成形した後、焼成して理論密度に対する相対密度が
９４．５〜９８．０％である一次焼結体とし、次いで、
該一次焼結体に熱間静水圧プレス処理を施して理論密度
に対する相対密度が９９．８％以上の二次焼結体とする
ことにより上記アルミナ焼結体を製造し、その後、該ア
ルミナ焼結体を切削工具形状に加工することを特徴とす
るアルミナセラミックス切削工具の製造方法。5. The method for producing an alumina ceramic cutting tool according to claim 1, wherein the alumina powder has an average particle size of 2.0 μm or less and a purity of 99.99% or more. After mixing with other raw material powders to form a predetermined shape, the mixture is fired to obtain a primary sintered body having a relative density of 94.5 to 98.0% with respect to the theoretical density.
The alumina sintered body is manufactured by subjecting the primary sintered body to hot isostatic pressing to form a secondary sintered body having a relative density with respect to the theoretical density of 99.8% or more. A method for manufacturing an alumina ceramic cutting tool, comprising processing the combined body into a cutting tool shape.
ルミナセラミックス切削工具の製造方法であって、 平均粒径が２．０μｍ以下であり純度が９９．９９％以
上であるアルミナ粉末を所定形状に成形した後、１２７
０〜１３６０℃で焼成して一次焼結体とし、次いで、該
一次焼結体に温度１２５０〜１５００℃、圧力５００〜
２０００ｋｇ／ｃｍ2の熱間静水圧プレス処理を施して
二次焼結体とすることにより上記アルミナ焼結体を製造
し、その後、該アルミナ焼結体を切削工具形状に加工す
ることを特徴とするアルミナセラミックス切削工具の製
造方法。6. The method for producing an alumina ceramic cutting tool according to claim 1, wherein the alumina powder has an average particle size of 2.0 μm or less and a purity of 99.99% or more. After molding into a predetermined shape, 127
The primary sintered body is fired at 0 to 1360 ° C. to obtain a primary sintered body.
The alumina sintered body is manufactured by performing a hot isostatic pressing process of 2000 kg / cm 2 to form a secondary sintered body, and thereafter, processing the alumina sintered body into a cutting tool shape. Method of manufacturing alumina ceramic cutting tools.
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| JP2000282215A JP2001322009A (en) | 1999-12-28 | 2000-09-18 | Alumina ceramic cutting tool and manufacturing method therefor |
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|---|---|---|---|
| JP37479799 | 1999-12-28 | ||
| JP2000062627 | 2000-03-07 | ||
| JP2000-62627 | 2000-03-07 | ||
| JP11-374797 | 2000-03-07 | ||
| JP2000282215A JP2001322009A (en) | 1999-12-28 | 2000-09-18 | Alumina ceramic cutting tool and manufacturing method therefor |
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|---|---|
| JP2001322009A true JP2001322009A (en) | 2001-11-20 |
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| Application Number | Title | Priority Date | Filing Date |
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Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2003034572A (en) * | 2001-07-23 | 2003-02-07 | Ngk Spark Plug Co Ltd | Alumina ceramic sintered body, its manufacturing method and cutting tool |
| JP2006087915A (en) * | 2004-08-27 | 2006-04-06 | Tosoh Corp | Orthodontic bracket and manufacturing method thereof |
| CN116003109A (en) * | 2022-12-05 | 2023-04-25 | 广东工业大学 | A kind of high-performance alumina ceramic chopper and preparation method thereof |
Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS58161969A (en) * | 1982-03-20 | 1983-09-26 | 日本特殊陶業株式会社 | Manufacture of ceramic tool for cutting tool |
| JPS6411183A (en) * | 1987-05-27 | 1989-01-13 | Minnesota Mining & Mfg | Abrasive grain made from ceramic containing aluminium oxide and rare earth metal, manufacture and product |
| JPH0450160A (en) * | 1990-06-19 | 1992-02-19 | Toshiba Tungaloy Co Ltd | Transparent alumina sintered material |
| JPH04193760A (en) * | 1990-11-26 | 1992-07-13 | Nkk Corp | Colored light-transmissive alumina sintered body and its production |
| JPH1171168A (en) * | 1997-06-26 | 1999-03-16 | Ngk Spark Plug Co Ltd | Alumina-based sintered ceramic material and its production |
-
2000
- 2000-09-18 JP JP2000282215A patent/JP2001322009A/en active Pending
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS58161969A (en) * | 1982-03-20 | 1983-09-26 | 日本特殊陶業株式会社 | Manufacture of ceramic tool for cutting tool |
| JPS6411183A (en) * | 1987-05-27 | 1989-01-13 | Minnesota Mining & Mfg | Abrasive grain made from ceramic containing aluminium oxide and rare earth metal, manufacture and product |
| JPH0450160A (en) * | 1990-06-19 | 1992-02-19 | Toshiba Tungaloy Co Ltd | Transparent alumina sintered material |
| JPH04193760A (en) * | 1990-11-26 | 1992-07-13 | Nkk Corp | Colored light-transmissive alumina sintered body and its production |
| JPH1171168A (en) * | 1997-06-26 | 1999-03-16 | Ngk Spark Plug Co Ltd | Alumina-based sintered ceramic material and its production |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2003034572A (en) * | 2001-07-23 | 2003-02-07 | Ngk Spark Plug Co Ltd | Alumina ceramic sintered body, its manufacturing method and cutting tool |
| JP2006087915A (en) * | 2004-08-27 | 2006-04-06 | Tosoh Corp | Orthodontic bracket and manufacturing method thereof |
| CN116003109A (en) * | 2022-12-05 | 2023-04-25 | 广东工业大学 | A kind of high-performance alumina ceramic chopper and preparation method thereof |
| CN116003109B (en) * | 2022-12-05 | 2023-10-31 | 广东工业大学 | High-performance alumina ceramic riving knife and preparation method thereof |
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