JP2007131493A - METHOD FOR PRODUCING BULK BODY OF Al-ADDED TiN - Google Patents
METHOD FOR PRODUCING BULK BODY OF Al-ADDED TiN Download PDFInfo
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本発明は、窒化チタン（ＴｉＮ）系化合物、特にＡｌ添加ＴｉＮのバルク体を製造する方法に関するものである。 The present invention relates to a method for producing a bulk body of titanium nitride (TiN) -based compounds, particularly Al-added TiN.
ＴｉＮ系化合物は、軽量であるにもかかわらず、高融点、高硬度並びに高耐食性、および高い化学的安定性等の優れた特性を有しており、また美しい金属光沢を示すので、機械部品や切削工具等あるいは宝飾部品に用いられている。
その一方で、ＴｉＮ系化合物は難焼結性の物質であるから、緻密なバルク体を製造することが難しく、これまで、主として薄膜材料として使用されてきている。
TiN-based compounds have excellent characteristics such as high melting point, high hardness and high corrosion resistance, and high chemical stability despite being lightweight, and exhibit a beautiful metallic luster, so that mechanical parts and Used for cutting tools and other jewelry parts.
On the other hand, TiN-based compounds are hardly sinterable substances, so that it is difficult to produce a dense bulk body, and until now, they have been mainly used as thin film materials.
従来技術として、ＴｉＮ系化合物、特にＡｌ添加ＴｉＮの粉末を焼結し、窒化チタンアルミ基焼結材を製造する方法が知られている（特許文献１参照）。
この従来の方法によれば、まず最初に、ＰＶＤ法（スパッタリング法やイオンプレーティング法）や、プラズマＣＶＤ法を用いて、（Ｔｉ１−ｘＡｌｘ）Ｎ（ｘ＝０．０５〜０．７０）の粉末が製造される。そして、（Ｔｉ１−ｘＡｌｘ）Ｎの粉末が、ＨＰ（ホットプレス）の他、例えば、ＨＩＰ（熱間等方加圧焼結）、超高圧ＨＩＰ等によって焼結され、窒化チタンアルミ基焼結材が得られる。
As a conventional technique, a method of manufacturing a titanium nitride aluminum-based sintered material by sintering a powder of TiN-based compound, particularly Al-added TiN is known (see Patent Document 1).
According to this conventional method, first, using a PVD method (sputtering method or ion plating method) or a plasma CVD method, (Ti 1-x Al x ) N (x = 0.05 to 0.00). 70) powder is produced. Then, the powder of (Ti 1-x Al x ) N is sintered by, for example, HIP (hot isostatic pressing), ultrahigh pressure HIP, etc. in addition to HP (hot press), and titanium nitride aluminum base A sintered material is obtained.
こうして得られた窒化チタンアルミ基焼結材は、高硬度であり、耐摩耗性、耐欠損性に優れ、例えば切削工具、掘削用ビット等に有効利用することができる。
しかしながら、この従来の方法では、原料となる（Ｔｉ１−ｘＡｌｘ）Ｎの粉末を製造するために、ＰＶＤ法やプラズマＣＶＤ法を使用するので、所定の組成ｘ＝０．０５〜０．７０を得るために、複雑な処理プロセスを必要とする。したがって、この方法は、（Ｔｉ１−ｘＡｌｘ）Ｎ（ｘ＝０．０５〜０．７０）の粉末の製造に、時間とコストを要し、量産性が低いという欠点を有している。
加えて、この方法によれば、（Ｔｉ１−ｘＡｌｘ）Ｎの粉末をＨＰ、ＨＩＰおよび超高圧ＨＩＰ等によって焼結するので、焼結体は、高い硬度を有している割に、曲げ強度が弱いという欠点を有している。
The titanium nitride aluminum-based sintered material thus obtained has high hardness and excellent wear resistance and fracture resistance, and can be effectively used for cutting tools, excavation bits, and the like.
However, in this conventional method, since a PVD method or a plasma CVD method is used to produce a raw material (Ti 1-x Al x ) N powder, a predetermined composition x = 0.05 to 0.00. In order to obtain 70, a complicated processing process is required. Therefore, this method has the disadvantages that it takes time and cost to produce a powder of (Ti 1-x Al x ) N (x = 0.05 to 0.70), and mass productivity is low. .
In addition, according to this method, since the powder of (Ti 1-x Al x ) N is sintered by HP, HIP, ultra-high pressure HIP, or the like, the sintered body has high hardness, It has the disadvantage of low bending strength.
したがって、本発明の課題は、従来よりも短時間にかつ低コストでＡｌ添加ＴｉＮのバルク体を製造する方法を提供することにある。
また、本発明の課題は、従来のものより曲げ強度の優れたＡｌ添加ＴｉＮのバルク体を製造する方法を提供することにある。
Accordingly, an object of the present invention is to provide a method for producing a bulk body of Al-added TiN in a shorter time and at a lower cost than before.
Moreover, the subject of this invention is providing the method of manufacturing the bulk body of Al addition TiN which was excellent in bending strength than the conventional one.
上記課題を解決するため、本発明は、（１）所定量の金属Ｔｉ粉末および所定量の金属Ａｌ粉末と、所定量の窒素含有化合物の粉末または所定量の液体状窒素含有化合物とを混合した後、プレス成形して第１の成形体とするステップと、（２）前記第１の成形体を自己燃焼合成させ、それによって得られた試料を粉砕して粉体とするステップと、（３）前記粉体をプレス成形して第２の成形体とするステップと、（４）前記第２の成形体を加圧焼結させることにより、Ａｌ添加ＴｉＮのバルク体を得るステップとからなっていることを特徴とするＡｌ添加ＴｉＮのバルク体を製造する方法を構成したものである。 In order to solve the above problems, the present invention (1) mixes a predetermined amount of metal Ti powder and a predetermined amount of metal Al powder with a predetermined amount of nitrogen-containing compound powder or a predetermined amount of liquid nitrogen-containing compound. And (2) a step of self-combusting and synthesizing the first molded body, and crushing the sample obtained thereby to form a powder; and (3) ) Press-molding the powder into a second compact, and (4) obtaining a bulk body of Al-added TiN by pressure-sintering the second compact. A method for producing a bulk body of Al-added TiN, characterized in that
上記課題を解決するため、また、本発明は、（１）所定量の金属Ｔｉ粉末および所定量の金属Ａｌ粉末を混合した後、プレス成形して第１の成形体とするステップと、（２）前記第１の成形体を所定圧のＮ２雰囲気中で自己燃焼合成させ、それによって得られた試料を粉砕して第１の粉体とするステップと、（３）前記第１の粉体をプレス成形して第２の成形体とするステップと、（４）前記第２の成形体を所定圧のＮ２雰囲気中で自己燃焼合成させ、それによって得られた試料を粉砕して第２の粉体とするステップと、（５）前記第２の粉体をプレス成形して第３の成形体とするステップと、（６）前記第３の成形体を加圧焼結させることにより、Ａｌ添加ＴｉＮのバルク体を得るステップとからなっていることを特徴とするＡｌ添加ＴｉＮのバルク体を製造する方法を構成したものである。 In order to solve the above problems, the present invention also includes (1) a step of mixing a predetermined amount of metal Ti powder and a predetermined amount of metal Al powder and then press-molding to form a first molded body; ) Self-combustion synthesis of the first compact in an N 2 atmosphere at a predetermined pressure, and pulverizing a sample obtained thereby to form a first powder; and (3) the first powder. (4) self-combustion synthesis of the second compact in an N 2 atmosphere at a predetermined pressure, and a sample obtained thereby is pulverized to form a second compact. (5) a step of press-molding the second powder into a third molded body, and (6) pressure-sintering the third molded body, An Al-added TN comprising a step of obtaining a bulk body of Al-added TiN Method for producing a bulk of N is obtained by constituting the.
上記の構成において、前記金属Ｔｉ粉末および金属Ａｌ粉末の量を、形成されるＡｌ添加ＴｉＮのバルク体の組成が（Ｔｉ１−ｘＡｌｘ）Ｎ（０＜ｘ≦０．０８）となるように選択することが好ましい。
また、前記加圧焼結は、通電加圧焼結であることが好ましく、さらには、前記通電加圧焼結を、真空中において圧力１０〜５０ＭＰａを加えた状態で、５０〜２００℃／分で１３００〜１９００℃まで昇温し、その温度を３〜２０分間保持した後、５０〜１００℃／分で降温するという条件下で実行することが好ましい。
In the above configuration, the amount of the metal Ti powder and the metal Al powder is set so that the composition of the bulk body of the Al-added TiN to be formed becomes (Ti 1-x Al x ) N (0 <x ≦ 0.08). It is preferable to select.
The pressure sintering is preferably electric current pressure sintering, and further, the electric current pressure sintering is performed at 50 to 200 ° C./min in a vacuum with a pressure of 10 to 50 MPa. It is preferable that the temperature is raised to 1300 to 1900 ° C., held for 3 to 20 minutes, and then lowered at 50 to 100 ° C./min.
本発明によれば、原料となる（Ｔｉ１−ｘＡｌｘ）Ｎの粉末を、金属Ｔｉ粉末および金属Ａｌ粉末を混合して成形体とし、それを自己燃焼合成させて得られた試料を粉砕することによって製造するようにしたので、所定の組成、好ましくは０＜ｘ≦０．２の（Ｔｉ１−ｘＡｌｘ）Ｎの粉末を短時間にかつ低コストで製造可能であり、従来法よりも量産性が格段に向上する。
さらに、本発明によれば、（Ｔｉ１−ｘＡｌｘ）Ｎの粉末を成形体とした後、加圧焼結させるようにしたので、得られた（Ｔｉ１−ｘＡｌｘ）Ｎのバルク体は、従来のものより緻密であり、曲げ強度等の物理的特性も向上している。
こうして、本発明によって製造される（Ｔｉ１−ｘＡｌｘ）Ｎのバルク体は、高い硬度に加えて大きな曲げ強度も備えているので、切削工具等として利用できるだけでなく、例えば、タービンエンジンのプロペラ等の形成材料として使用することもできる。
According to the present invention, a raw material (Ti 1-x Al x ) N powder is mixed with a metal Ti powder and a metal Al powder to form a molded body, and a sample obtained by self-combustion synthesis is pulverized. Thus, it is possible to manufacture a powder of (Ti 1-x Al x ) N having a predetermined composition, preferably 0 <x ≦ 0.2, in a short time and at a low cost. The mass productivity is greatly improved.
Furthermore, according to the present invention, since the powder of (Ti 1-x Al x ) N is formed into a compact and then sintered under pressure, the resulting bulk of (Ti 1-x Al x ) N is obtained. The body is denser than conventional ones and has improved physical properties such as bending strength.
Thus, the bulk body of (Ti 1-x Al x ) N produced by the present invention has not only high hardness but also high bending strength, so it can be used not only as a cutting tool or the like, It can also be used as a forming material for propellers and the like.
次に、本発明の好ましい実施例について説明する。
本発明によれば、まず、所定量の金属Ｔｉ粉末（純度９９．９％：平均粒径＝２５μｍ）および所定量の金属Ａｌ粉末（純度９９．８９％：平均粒径＝１．１５μｍ）が湿式混合される。この場合、湿式混合がより好ましいが、乾式混合することもできる。そして、その混合された粉体が、一軸加圧成形された後、１００ＭＰａで冷間静水圧プレス（ＣＩＰ）されて第１の成形体とされる。
Next, preferred embodiments of the present invention will be described.
According to the present invention, first, a predetermined amount of metal Ti powder (purity 99.9%: average particle size = 25 μm) and a predetermined amount of metal Al powder (purity 99.89%: average particle size = 1.15 μm) are obtained. Wet mixed. In this case, wet mixing is more preferable, but dry mixing can also be performed. The mixed powder is uniaxially pressed and then cold isostatic pressed (CIP) at 100 MPa to form a first molded body.
次に、この第１の成形体が、１０ＭＰａのＮ２（純度９９．９９％）雰囲気中で自己燃焼合成（Self-propagating High-temperature Synthesis:ＳＨＳ） せしめられる。この自己燃焼合成によって得られた試料は、超硬乳鉢によって粉砕され、メッシュフィルター（開口径３２μｍ）を用いて整粒され、第１の粉体とされる。
第１の粉体は、再び、一軸加圧成形された後、１００ＭＰａでＣＩＰされて第２の成形体とされ、前と同様に自己燃焼合成せしめられる。この自己燃焼合成によって得られた試料は、前と同様、超硬乳鉢によって粉砕され、メッシュフィルターを用いて整粒され、第２の粉体とされる。
Next, this first molded body is subjected to self-propagating high-temperature synthesis (SHS) in a 10 MPa N 2 (purity 99.99%) atmosphere. A sample obtained by this self-combustion synthesis is pulverized by a cemented mortar and sized using a mesh filter (opening diameter: 32 μm) to form a first powder.
The first powder is again uniaxially pressed and then CIPed at 100 MPa to form a second molded body, which is self-combusted and synthesized as before. The sample obtained by this self-combustion synthesis is pulverized with a cemented mortar as before, and is sized using a mesh filter to form a second powder.
この実施例では、上述のように自己燃焼合成が２回繰り返されるが、自己燃焼合成を１回だけ行うようにしてもよい。この場合、金属チタンＴｉおよび金属アルミニウムＡｌ粉末の混合物からなる成形体中の金属粒子間の隙間を充填する気体の窒素ガス、および成形体周辺に存在する窒素ガスからの窒素供給では、自己燃焼合成一回の当たりの窒素の供給量に限界がある。そこで、ＴｉＮ化合物を生成するには略５０モル％（窒素含有量として２２．６４質量％）の窒素を供給するために必要な窒素を、気体状態ではなく、液体や固体状態で供給する必要がある。例えば、ジアゾ化ナトリウムＮａＮ３のような固体の化合物を原料のＴｉやＡｌ粉末と適当量混合し、この混合物の成形体を自己燃焼させればよい。燃焼反応後のＮａは温水で洗浄して洗い流せば除去できる。 In this embodiment, the self-combustion synthesis is repeated twice as described above, but the self-combustion synthesis may be performed only once. In this case, self-combustion synthesis is performed by supplying nitrogen gas from a gas filling a gap between metal particles in a molded body made of a mixture of metal titanium Ti and metal aluminum Al powder, and nitrogen gas existing around the molded body. There is a limit to the amount of nitrogen supplied per time. Therefore, in order to produce a TiN compound, it is necessary to supply the nitrogen necessary for supplying approximately 50 mol% (nitrogen content 22.64% by mass) of nitrogen in a liquid or solid state, not in a gaseous state. is there. For example, an appropriate amount of a solid compound such as sodium diazotized NaN 3 may be mixed with the raw material Ti or Al powder, and the compact of this mixture may be self-combusted. Na after the combustion reaction can be removed by washing with warm water and washing away.
第２の粉体は、その後、遊星ボールミル（ＷＣ−Ｃｏボール使用、５００ｒｐｍ、６０分）によって粉砕され、さらに乾燥された後、２００ＭＰａでＣＩＰ成形されて第３の成形体とされる。
その後、第３の成形体は、通電加圧焼結（Spark Plasma Sintering：ＳＰＳ）せしめられ、それによってＡｌ添加ＴｉＮのバルク体が得られる。通電加圧焼結は、真空中において圧力１０〜５０ＭＰａを加えた状態で、５０〜２００℃／分で１３００〜１９００℃まで昇温し、その温度を３〜２０分間保持した後、５０〜１００℃／分で降温するという条件下でなされる。この実施例では、（Ｔｉ１−ｘＡｌｘ）Ｎの粉末を通電加圧焼結によって焼結させたが、ＨＩＰ（熱間等方加圧焼結）等の加圧焼結によって焼結させてもよい。
Thereafter, the second powder is pulverized by a planetary ball mill (using WC-Co balls, 500 rpm, 60 minutes), further dried, and then CIP-molded at 200 MPa to form a third compact.
Thereafter, the third molded body is subjected to electric current pressure sintering (Spark Plasma Sintering: SPS), thereby obtaining a bulk body of Al-added TiN. In the electric current pressure sintering, the temperature is increased to 1300 to 1900 ° C. at 50 to 200 ° C./min with a pressure of 10 to 50 MPa in a vacuum, and the temperature is maintained for 3 to 20 minutes. It is made under the condition that the temperature is lowered at a rate of ° C / min. In this example, the powder of (Ti 1-x Al x ) N was sintered by electric current pressure sintering, but was sintered by pressure sintering such as HIP (hot isostatic pressing). May be.
本発明によれば、形成されるＡｌ添加ＴｉＮのバルク体の組成（Ｔｉ１−ｘＡｌｘ）Ｎは、主として、混合される金属Ｔｉ粉末および金属Ａｌ粉末の量によって決定される。
そして、それぞれ、ｘ＝０、ｘ＝０．０１、ｘ＝０．０２、ｘ＝０．０４、ｘ＝０．０８の組成を有する５種類の（Ｔｉ１−ｘＡｌｘ）Ｎのバルク体（試料Ｎｏ．１〜Ｎｏ．５）を製造した。なお、これらのバルク体試料の製造に際しては、通電加圧焼結は、真空中において圧力約３０ＭＰａを加えた状態で、約１００℃／分で１３００〜１９００℃まで昇温し、その温度を約５分間保持した後、約５０℃／分で降温するという条件下でなされた。
According to the present invention, the composition (Ti 1-x Al x ) N of the bulk body of Al-added TiN to be formed is mainly determined by the amount of mixed metal Ti powder and metal Al powder.
Then, five kinds of (Ti 1-x Al x ) N bulk bodies having compositions of x = 0, x = 0.01, x = 0.02, x = 0.04, and x = 0.08, respectively. (Sample No. 1 to No. 5) were manufactured. In the production of these bulk body samples, energization and pressure sintering is carried out by raising the temperature to 1300-1900 ° C. at about 100 ° C./min with a pressure of about 30 MPa applied in a vacuum. After holding for 5 minutes, the temperature was lowered at about 50 ° C./minute.
製造した各バルク体試料の結晶構造、すなわち、その結晶相をＸ線回折装置によって分析した。図１には、Ｘ線回折パターン（ＣｕＫα線による）のグラフが示してある。グラフの縦軸はＸ線強度、横軸は回折角２θの値をそれぞれ表している。なお、図１では、試料Ｎｏ．２のデータは省略されている。
図１のグラフから、試料Ｎｏ．１（ｘ＝０）では、立方晶ＴｉＮが形成され、試料Ｎｏ．３（ｘ＝０．０２）では、（Ｔｉ１−ｘＡｌｘ）Ｎが形成されていることがわかる。また、試料Ｎｏ．４（ｘ＝０．０４）および試料Ｎｏ．５（ｘ＝０．０８）では、（Ｔｉ１−ｘＡｌｘ）Ｎのほかに微細窒化物Ｔｉ２ＡｌＮが形成されている。
The crystal structure of each manufactured bulk body sample, that is, the crystal phase thereof was analyzed by an X-ray diffractometer. FIG. 1 shows a graph of an X-ray diffraction pattern (by CuK α- ray). The vertical axis of the graph represents the X-ray intensity, and the horizontal axis represents the value of the diffraction angle 2θ. In FIG. Data 2 is omitted.
From the graph of FIG. 1 (x = 0), cubic TiN is formed. 3 (x = 0.02), it can be seen that (Ti 1-x Al x ) N is formed. Sample No. 4 (x = 0.04) and sample no. In 5 (x = 0.08), fine nitride Ti 2 AlN is formed in addition to (Ti 1-x Al x ) N.
また、各バルク体試料の諸特性を調べ、結果を以下の表１にまとめた。
表１を参照して、Ａｌの添加量（ｘの値）が増大するにつれて、格子定数ａが、立方晶ＴｉＮの格子定数４．２４１１Åから４．２３２５Åへと徐々に減少し、ここでも（Ｔｉ１−ｘＡｌｘ）Ｎの形成が裏付けられた。また、Ａｌの添加量（ｘの値）が増大するにつれて、バルク体の曲げ強度σｂが増大していることがわかる。そして、最も優れた機械的特性を示したものは、試料５（ｘ＝０．０８）で、硬度ＨＶ＝１４．１ＧＰａ、曲げ強度σｂ＝７９６ＭＰａ、破壊靱性値ＫＩＣ＝４．５ＭＰａ・ｍ１／２である。この結果から、Ａｌを添加することによって、硬度および破壊靱性値はわずかに低下するものの、曲げ強度が著しく向上することがわかる。 Referring to Table 1, as the additive amount of Al (the value of x) increases, the lattice constant a gradually decreases from the cubic TiN lattice constant of 4.2411 Å to 4.2325 、. The formation of 1-x Al x ) N was confirmed. It can also be seen that the bending strength σ b of the bulk body increases as the additive amount of Al (value of x) increases. Sample 5 (x = 0.08) showed the most excellent mechanical properties, hardness H V = 14.1 GPa, bending strength σ b = 796 MPa, fracture toughness value K IC = 4.5 MPa · m 1/2 . From this result, it can be seen that, by adding Al, although the hardness and fracture toughness values are slightly decreased, the bending strength is remarkably improved.
Claims (5)
（２）前記第１の成形体を自己燃焼合成させ、それによって得られた試料を粉砕して粉体とするステップと、
（３）前記粉体をプレス成形して第２の成形体とするステップと、
（４）前記第２の成形体を加圧焼結させることにより、Ａｌ添加ＴｉＮのバルク体を得るステップとからなっていることを特徴とするＡｌ添加ＴｉＮのバルク体を製造する方法。 (1) A predetermined amount of metal Ti powder and a predetermined amount of metal Al powder mixed with a predetermined amount of nitrogen-containing compound powder or a predetermined amount of liquid nitrogen-containing compound, and then press-molded to form a first molded body. And steps
(2) self-combusting and synthesizing the first molded body, and pulverizing a sample obtained thereby to form a powder;
(3) a step of press-molding the powder into a second molded body;
(4) A method for producing an Al-added TiN bulk body, comprising the step of obtaining a bulk body of Al-added TiN by pressure sintering the second compact.
（２）前記第１の成形体を所定圧のＮ２雰囲気中で自己燃焼合成させ、それによって得られた試料を粉砕して第１の粉体とするステップと、
（３）前記第１の粉体をプレス成形して第２の成形体とするステップと、
（４）前記第２の成形体を所定圧のＮ２雰囲気中で自己燃焼合成させ、それによって得られた試料を粉砕して第２の粉体とするステップと、
（５）前記第２の粉体をプレス成形して第３の成形体とするステップと、
（６）前記第３の成形体を加圧焼結させることにより、Ａｌ添加ＴｉＮのバルク体を得るステップとからなっていることを特徴とするＡｌ添加ＴｉＮのバルク体を製造する方法。 (1) a step of mixing a predetermined amount of metal Ti powder and a predetermined amount of metal Al powder and then press-molding to form a first molded body;
(2) subjecting the first molded body to self-combustion synthesis in an N 2 atmosphere of a predetermined pressure, and pulverizing a sample obtained thereby to form a first powder;
(3) a step of press-molding the first powder into a second molded body;
(4) self-combusting and synthesizing the second molded body in an N 2 atmosphere at a predetermined pressure, and pulverizing a sample obtained thereby to form a second powder;
(5) a step of press-molding the second powder into a third molded body;
(6) A method for producing an Al-added TiN bulk body comprising the step of pressure sintering the third compact to obtain an Al-added TiN bulk body.
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Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2014104461A1 (en) * | 2012-12-31 | 2014-07-03 | 부산대학교 산학협력단 | Method for preparing ti2aln bulk material and micro electrical discharge machining method |
| KR101459196B1 (en) * | 2012-12-31 | 2014-11-07 | 부산대학교 산학협력단 | Manufacturing Methods of MAX Phases TiAlN Bulk Materials and Micro Electrical Discharge Drilling Method threeof |
| US10029948B2 (en) | 2014-08-29 | 2018-07-24 | Sumitomo Electric Industries, Ltd. | Sintered material, tool including sintered material, and sintered material production method |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0578107A (en) * | 1991-09-19 | 1993-03-30 | Yoshikiyo Ogino | Nitride powder |
| JPH05254939A (en) * | 1992-03-13 | 1993-10-05 | Osamu Yamada | Production of high density solid solution |
| JPH06271901A (en) * | 1993-03-17 | 1994-09-27 | Toyo Alum Kk | Ti-al intermetallic compound powder having excellent sinterability and sintered compact thereof |
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2005
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Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0578107A (en) * | 1991-09-19 | 1993-03-30 | Yoshikiyo Ogino | Nitride powder |
| JPH05254939A (en) * | 1992-03-13 | 1993-10-05 | Osamu Yamada | Production of high density solid solution |
| JPH06271901A (en) * | 1993-03-17 | 1994-09-27 | Toyo Alum Kk | Ti-al intermetallic compound powder having excellent sinterability and sintered compact thereof |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2014104461A1 (en) * | 2012-12-31 | 2014-07-03 | 부산대학교 산학협력단 | Method for preparing ti2aln bulk material and micro electrical discharge machining method |
| KR101459196B1 (en) * | 2012-12-31 | 2014-11-07 | 부산대학교 산학협력단 | Manufacturing Methods of MAX Phases TiAlN Bulk Materials and Micro Electrical Discharge Drilling Method threeof |
| US10029948B2 (en) | 2014-08-29 | 2018-07-24 | Sumitomo Electric Industries, Ltd. | Sintered material, tool including sintered material, and sintered material production method |
| US10501377B2 (en) | 2014-08-29 | 2019-12-10 | Sumitomo Electric Industries, Ltd. | Sintered material, tool including sintered material, and sintered material production method |
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| JP5093433B2 (en) | 2012-12-12 |
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