JP2010248615A - Molybdenum alloy and method for manufacturing the same - Google Patents
Molybdenum alloy and method for manufacturing the same Download PDFInfo
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Description
本発明は、高温炉用ヒータ並びにプレートやボルト、ナット、ピン等の高温用構造材料、更にはサファイア溶解用ルツボ等に代表される、１５００℃以上の高温において強度が要求される高温環境で使用される部材で、その部材の材料として使用されるモリブデン合金およびその製造方法に関するものである。 The present invention is used in a high-temperature environment where strength is required at a high temperature of 1500 ° C. or more, represented by a high-temperature furnace heater and a high-temperature structural material such as a plate, bolt, nut and pin, and a sapphire melting crucible. The present invention relates to a molybdenum alloy used as a material of the member and a method for manufacturing the same.
Ｗ，Ｍｏ，Ｒｅ（レニウム）およびこれらの合金は２０００℃以上の融点を有し、主に電子部品、電極材、フィラメント材として従来用いられてきたが、近年、その優れた高温強度、耐食性に着目された構造用部材の材料としての用途が期待されている。しかし、Ｗ，Ｍｏ，Ｒｅは融点が非常に高く、かつ、加工性が悪いため、通常の溶解・加工といった方法で製品を作ることは困難であった。したがって、一般には粉末焼結法により各種部材を製造しているのが現状である。 W, Mo, Re (rhenium) and their alloys have a melting point of 2000 ° C. or higher and have been conventionally used mainly as electronic parts, electrode materials, and filament materials, but in recent years, their excellent high-temperature strength and corrosion resistance have been achieved. It is expected to be used as a material for a structural member that has attracted attention. However, since W, Mo, and Re have a very high melting point and poor workability, it has been difficult to produce a product by a usual method such as melting and processing. Therefore, in general, various members are manufactured by a powder sintering method.
しかしながら、一般的な粉末焼結法で得られる焼結体の相対密度は９０％程度で、その内部には多数の気孔が残留している。これら金属焼結体の強度や耐食性等の特性は密度に大きく依存することが知られており焼結体内部の気泡は強度を著しく低下させたり、内部の気泡に腐食性溶液やガスが浸透し耐食性を著しく害する結果となる。一方、焼結温度が高すぎると結晶粒が粗大化し強度が低下し脆くなるという問題がある。したがって、通常は熱間圧延、熱間鍛造といった塑性加工により高密度化を図っているのが実状である。 However, the relative density of a sintered body obtained by a general powder sintering method is about 90%, and a large number of pores remain inside. It is known that the properties such as strength and corrosion resistance of these metal sintered bodies are greatly dependent on the density, and bubbles inside the sintered body significantly reduce the strength, or corrosive solution or gas penetrates into the internal bubbles. As a result, the corrosion resistance is significantly impaired. On the other hand, if the sintering temperature is too high, there is a problem that the crystal grains are coarsened, the strength is lowered, and it becomes brittle. Therefore, the actual situation is that high density is usually achieved by plastic working such as hot rolling and hot forging.
上述した問題を解消する方法として、例えば特開平６−１２８６０４号公報（特許文献１）に開示されているように、マトリックスとなるマトリックス金属粉末とこのマトリックス金属粉末よりも酸化物生成自由エネルギーが小さい金属酸化物粉末（Ｙ，Ｓｃ，Ｎｄ，Ｇｄ，Ｔｈ，Ｄｙ，Ｅｒ，Ｃｅ，Ｌｕ，Ｈｏ，Ａｌ，Ｔｍ，Ｚｒ，Ｈｆ，Ｃａ，Ｍｇといった金属の酸化物からなる粉末）を化学量論組成よりも酸素量が低い状態で混合後、焼結する金属材料の製造方法が提案されている。
しかし、上述した特許文献１のように焼結した金属材料でも、必ずしも十分な強度を得るまでには至っていない。これらの問題を解消するために、発明者らは鋭意開発を進めた結果、実用強度に影響を及ぼすモリブデンの結晶粒の急激な粗大化が始まる１５００℃以上の温度での使用においても、強度は従来品以上で、かつ結晶粒の粗大化を抑制し、強度の低下を防止するモリブデン合金およびその製造方法を提供するものである。 However, even a sintered metal material as in Patent Document 1 described above does not necessarily achieve sufficient strength. In order to solve these problems, the inventors have intensively developed, and as a result, the strength is not limited even when used at a temperature of 1500 ° C. or higher, at which a rapid coarsening of molybdenum crystal grains affecting practical strength begins. The present invention provides a molybdenum alloy that is higher than conventional products, suppresses the coarsening of crystal grains, and prevents a decrease in strength, and a method for producing the same.
その発明の要旨とするところは、
（１）Ｔｉ、Ｚｒ、Ｈｆの炭化物、硼化物、窒化物、酸化物の１種または２種以上、または／およびＶ、Ｎｂ、Ｔａ、ＣｒおよびＷの１種または２種以上の添加粉末を、マトリックスとなるモリブデン粉末に対し、０．１〜２０質量％混合し、固化成形してなることを特徴とするモリブデン合金。
The gist of the invention is that
(1) One or more of Ti, Zr, and Hf carbides, borides, nitrides, oxides, and / or one or more additive powders of V, Nb, Ta, Cr, and W A molybdenum alloy obtained by mixing 0.1 to 20% by mass and solidifying and molding the molybdenum powder as a matrix.
（２）前記（１）に記載したマトリックスのモリブデン粉末の平均粒径が６〜２０μｍであることを特徴とするモリブデン合金。
（３）前記（１）または（２）に記載の添加粉末として、平均粒径が０．５〜５μｍであることを特徴とするモリブデン合金。
(2) A molybdenum alloy characterized in that the average particle size of the molybdenum powder of the matrix described in (1) is 6 to 20 μm.
(3) A molybdenum alloy having an average particle size of 0.5 to 5 μm as the additive powder according to (1) or (2).
（４）前記（１）〜（３）のいずれか１項に記載の混合粉末をＨＩＰにて固化成形することを特徴とするモリブデン合金の製造方法。
（５）前記（４）に記載したＨＩＰ処理として、処理温度１１００〜２１００℃、圧力５０〜３００ＭＰａとなる条件にて、保持を３０分〜２４時間行うことを特徴とするモリブデン合金の製造方法にある。
(4) A method for producing a molybdenum alloy, wherein the mixed powder according to any one of (1) to (3) is solidified and formed by HIP.
(5) As a HIP process described in the above (4), a method for producing a molybdenum alloy characterized in that holding is performed for 30 minutes to 24 hours under conditions of a processing temperature of 1100 to 2100 ° C. and a pressure of 50 to 300 MPa. is there.
以上述べたように、本発明による高融点かつモリブデン中で熱力学的に安定な金属またはセラミックスを、モリブデン中へ微細分散させ、ＨＩＰすることにより、１５００℃以上の温度域の結晶粒成長を抑制し、高強度な成形体を得るモリブデン合金およびその製造を可能とした。 As described above, the high melting point and thermodynamically stable metal or ceramic in molybdenum according to the present invention is finely dispersed in molybdenum and HIPed to suppress crystal grain growth in a temperature range of 1500 ° C. or higher. As a result, a molybdenum alloy for obtaining a high-strength molded body and the production thereof were made possible.
以下、本発明について詳細に説明する。
本発明に係るＴｉ、Ｚｒ、Ｈｆの炭化物、硼化物、窒化物、酸化物としては、ＴｉＣ、ＴｉＢ2 、ＴｉＮ、ＴｉＯ2 、ＺｒＣ、ＺｒＢ2 、ＺｒＮ、ＺｒＯ2 、ＨｆＣ、ＨｆＢ2 、ＨｆＮ、ＨｆＯ2 等をいう。また、上記Ｔｉ、Ｚｒ、Ｈｆの炭化物、硼化物、窒化物、酸化物とＶ、Ｎｂ、Ｔａ、ＣｒおよびＷをマトリックスに対して第二相となる添加粉末とした理由は、第１に高温で溶融しないこと、第２にモリブデンと反応しにくく、かつ固溶しにくいこと、第３に熱力学的に安定であることの３つの条件を満たす第二相粒子を分散させることにより、マトリックスのモリブデン相の結晶粒粗大化を抑制することにある。ただし、その添加量が０．１％未満では粗大化抑制効果が見られず、２０％を超えると材料が脆化するため抗折強度が劣化する。
Hereinafter, the present invention will be described in detail.
Examples of carbides, borides, nitrides, and oxides of Ti, Zr, and Hf according to the present invention include TiC, TiB 2 , TiN, TiO 2 , ZrC, ZrB 2 , ZrN, ZrO 2 , HfC, HfB 2 , HfN, HfO 2 etc. The reason why Ti, Zr, Hf carbides, borides, nitrides, oxides, and V, Nb, Ta, Cr, and W are added powders as a second phase with respect to the matrix is mainly because of the high temperature. By dispersing the second phase particles satisfying the three conditions of not melting at the second layer, secondly not easily reacting with molybdenum and hardly dissolved, and thirdly being thermodynamically stable. The purpose is to suppress coarsening of crystal grains in the molybdenum phase. However, if the addition amount is less than 0.1%, the effect of suppressing the coarsening is not seen, and if it exceeds 20%, the material becomes brittle and the bending strength deteriorates.
マトリックスとなるモリブデン粉末の平均粒径を６〜２０μｍとした理由は、マトリックスのモリブデン粉末の平均粒径が微細すぎると、成形時の充填が極度に悪くなり実用として要求されるに十分な密度が得られず強度不足となるためである。それに対し平均粒径が大きいと、第二相の分散状態が悪くなり、強度不足となるためである。また、添加粉末の平均粒径を０．５〜５μｍの粉末であるとした理由は、微細すぎるとマトリックスの結晶成長の抑制への効果が低く、一方で平均粒径が５μｍを超えるとマトリックスに第二相を微細に分散させることが出来ないため、いずれも強度不足となるためである。このように添加粉末がモリブデン中で微細に、かつ、多数残留することで、高温におけるモリブデン相の結晶成長を抑制するピン止め効果を発現させ、強度を改善するものである。なお、モリブデン粉末および添加粉末の平均粒径はレーザー回折法による測定によるも のである。 The reason why the average particle size of the molybdenum powder used as the matrix is set to 6 to 20 μm is that if the average particle size of the molybdenum powder of the matrix is too fine, the filling at the time of molding becomes extremely poor and the density sufficient for practical use is obtained. This is because it is not obtained and the strength is insufficient. On the other hand, when the average particle size is large, the dispersion state of the second phase is deteriorated and the strength is insufficient. The reason why the average particle size of the additive powder is 0.5-5 μm is that if it is too fine, the effect of suppressing the crystal growth of the matrix is low, while if the average particle size exceeds 5 μm, This is because the second phase cannot be finely dispersed, and in any case, the strength is insufficient. As described above, when the additive powder remains fine and numerous in the molybdenum, a pinning effect for suppressing the crystal growth of the molybdenum phase at a high temperature is exhibited and the strength is improved. The average particle size of the molybdenum powder and additive powder is measured by laser diffraction method.
モリブデン合金をＨＩＰにて固化成形するもので、ＨＩＰ処理として、処理温度１１００〜２１００℃、圧力５０〜３００ＭＰａとなる条件にて、３０分〜２４時間保持のＨＩＰ処理を行う。処理温度が、１１００℃未満では密度が不足し、また、２１００℃を超える温度を得るためには実用設備上コストアップとなることから、その範囲を１１００〜２１００℃とした。なお、ＨＩＰ処理温度が、１４００℃を超える条件では、ＳＣ製容器が処理温度により溶融するため、市販のモリブデンやニオブやタンタルなど高融点材料の板を使って上記ＳＣ製容器と同寸法の容器を作製し、ＨＩＰ処理に用いることが好ましい。 A molybdenum alloy is solidified and formed by HIP. As HIP processing, HIP processing is performed for 30 minutes to 24 hours under conditions of a processing temperature of 1100 to 2100 ° C. and a pressure of 50 to 300 MPa. When the processing temperature is less than 1100 ° C., the density is insufficient, and in order to obtain a temperature exceeding 2100 ° C., the cost is increased in practical equipment, so the range is set to 1100-2100 ° C. Under the condition that the HIP processing temperature exceeds 1400 ° C., the SC container melts depending on the processing temperature. Therefore, a container having the same dimensions as the above SC container is obtained using a commercially available high melting point material such as molybdenum, niobium or tantalum. Is preferably used for HIP treatment.
圧力５０〜３００ＭＰａとした理由は、５０ＭＰａ未満では十分な密度を得ることが出来ず、また、３００ＭＰａを超える温度を得るためには実用設備上コストアップとなることから、その範囲を５０〜３００ＭＰａとした。さらに、３０分〜２４時間保持とした理由は、３０分未満では十分な密度を得ることが出来ず、また２４時間を超えると結晶粒が粗大化することから、その処理保持時間を３０分〜２４時間とした。好ましくは、処理温度１２００〜１７００℃、圧力１００〜２００ＭＰａ、処理時間１〜１０時間保持である。 The reason why the pressure is set to 50 to 300 MPa is that a sufficient density cannot be obtained if the pressure is less than 50 MPa, and in order to obtain a temperature exceeding 300 MPa, the cost is increased in practical equipment. did. Furthermore, the reason why the holding time is 30 minutes to 24 hours is that a sufficient density cannot be obtained if the time is less than 30 minutes, and if the time exceeds 24 hours, the crystal grains are coarsened. 24 hours. Preferably, the treatment temperature is 1200 to 1700 ° C., the pressure is 100 to 200 MPa, and the treatment time is 1 to 10 hours.
以下、本発明について実施例によって具体的に説明する。
表１に示すモリブデン粉末に対する各種添加粉末を混合した組成の粉末２０ｋｇを直径２５０ｍｍで高さ８０ｍｍの円柱形状のＳＣ製容器に脱気封入し、処理温度１３００℃、圧力１００ＭＰａ、５時間保持、圧力媒体ＡｒのＨＩＰ処理条件にて、直径２００ｍｍで厚さ４０ｍｍの成形体を作製した。上記成形体を実使用環境に合わせた評価のために、カーボンヒーターを用いて不活性雰囲気にて、２０００℃、５時間の熱処理を実施した。上記２０００℃の熱処理を施した成形体より、テストピースを作製し、その評価としてマトリックス部であるモリブデンの結晶粒径および抗折強度で示した。その結果を表２に示す。なお、結晶粒の評価としては、研磨面を腐食し光学顕微鏡写真を撮影し、この写真に一定長さの試験直線を引き、この直線と結晶粒界との交点の数を測定し、［試験直線長さ（μｍ）］／［交点の数（個）］により評価した。これを、１３００℃にて５時間ＨＩＰした純モリブデン成形体の結晶粒径を１００と規定し、相対評価した。また、強度の指標としては、３点曲げ試験における抗折強度を測定し、１３００℃にて５時間ＨＩＰした純モリブデン成形体の抗折強度を１００と規定し、相対評価した。抗折強度は、２×２×２０ｍｍの試験片により評価した。
Hereinafter, the present invention will be specifically described with reference to examples.
20 kg of a powder having a composition in which various additive powders are mixed with the molybdenum powder shown in Table 1 was deaerated and sealed in a cylindrical SC container having a diameter of 250 mm and a height of 80 mm, a processing temperature of 1300 ° C., a pressure of 100 MPa, and a holding time of 5 hours. A molded body having a diameter of 200 mm and a thickness of 40 mm was produced under the HIP treatment conditions of the medium Ar. In order to evaluate the molded body in accordance with the actual use environment, a heat treatment was performed at 2000 ° C. for 5 hours in an inert atmosphere using a carbon heater. A test piece was prepared from the molded body subjected to the heat treatment at 2000 ° C., and the evaluation was shown by the crystal grain size and the bending strength of molybdenum as the matrix portion. The results are shown in Table 2. For the evaluation of crystal grains, the polished surface was corroded and an optical microscope photograph was taken, a test straight line having a certain length was drawn on this photograph, and the number of intersections between this straight line and the crystal grain boundary was measured. Evaluation was carried out by [Linear length (μm)] / [Number of intersections (number)] The crystal grain size of a pure molybdenum molded body that was HIPed at 1300 ° C. for 5 hours was defined as 100 and subjected to relative evaluation. In addition, as an index of strength, the bending strength in a three-point bending test was measured, and the bending strength of a pure molybdenum molded body HIPed at 1300 ° C. for 5 hours was defined as 100, and relative evaluation was performed. The bending strength was evaluated using a 2 × 2 × 20 mm test piece.
表２に示すように、比較例試料Ｎｏ．３７、３８、４０、４３、４５はいずれも表１のように添加粉末量が少なく、かつ、試料Ｎｏ．３７はＭｏ粉末粒径が小さく、試料Ｎｏ．３８、４０はＭｏ粉末粒径が大きく、試料Ｎｏ．４３、４５は添加粉末の粒径が大きいため、いずれも抗折強度が劣る。比較例試料Ｎｏ．３９、４１、４２、４４、４６〜４８はいずれも表１のように添加粉末量が多く、かつ、試料Ｎｏ．３９はＭｏ粉末粒径が大きく、試料Ｎｏ．４１は添加粉末粒径が小さく、試料Ｎｏ．４２は添加粉末粒径が大きく、試料Ｎｏ．４６〜４８はＭｏ粉末粒径と添加粉末粒径がともに大きいため、いずれも抗折強度が劣る。 As shown in Table 2, Comparative Sample No. 37, 38, 40, 43 and 45 all have a small amount of added powder as shown in Table 1, and sample No. No. 37 has a small Mo powder particle size. Nos. 38 and 40 have a large Mo powder particle size. 43 and 45 are inferior in bending strength because the additive powder has a large particle size. Comparative sample No. Nos. 39, 41, 42, 44, and 46 to 48 have a large amount of added powder as shown in Table 1, and sample Nos. No. 39 has a large Mo powder particle size. No. 41 has a small additive powder particle size. No. 42 has a large additive powder particle size. Nos. 46 to 48 are inferior in bending strength because both the Mo powder particle size and the additive powder particle size are large.
比較例試料Ｎｏ．４９、５０は表１のように添加粉末量が多いため抗折強度が劣る。比較例試料Ｎｏ．５１はＭｏ粉末粒径が小さく、比較例試料Ｎｏ．５２はＭｏ粉末粒径が大きく、比較例試料Ｎｏ．５３は添加粉末粒径が小さく、比較例試料Ｎｏ．５４は添加粉末粒径が大きいため、いずれも抗折強度が劣る。これに対し、本発明例試料Ｎｏ．１〜３６はいずれも添加粉末の添加量、モリブデン粉末の平均粒径、および添加粉末平均粒径が本発明の条件を満たしていることから、これらはいずれもマトリックスであるモリブデンの結晶粒径が細かく、抗折強度に優れていることが分かる。 Comparative sample No. Nos. 49 and 50 are inferior in bending strength because of the large amount of added powder as shown in Table 1. Comparative sample No. No. 51 has a small Mo powder particle size. No. 52 has a large Mo powder particle size. No. 53 has a small additive powder particle size. Since No. 54 has a large additive powder particle size, all have poor bending strength. On the other hand, the present invention sample No. 1 to 36 all have the additive amount of the additive powder, the average particle diameter of the molybdenum powder, and the average particle diameter of the additive powder satisfy the conditions of the present invention. It can be seen that it is fine and excellent in bending strength.
次に、ＨＩＰ条件を変化させた場合の実施例および比較例を示す。組成Ｎｏ．３の添加粉末の添加量で、Ｍｏ結晶粉末粒径が１８μｍ、添加粉末平均粒径４μｍの条件で、ＨＩＰ処理の温度、圧力、保持時間を表３のように変化させ、結晶粒径および抗折強度を評価した。これらの評価方法は前述の通りである。なお、表３には評価結果も併せて示す。 Next, examples and comparative examples when the HIP conditions are changed will be described. Composition No. With the addition amount of the additive powder of 3, the crystal grain size and the resistance of the HIP treatment were changed as shown in Table 3 under the conditions of the Mo crystal powder particle size of 18 μm and the additive powder average particle size of 4 μm. Folding strength was evaluated. These evaluation methods are as described above. Table 3 also shows the evaluation results.
表３に示すように、比較例Ｎｏ．１０２は処理温度が低いために抗折強度が低い。比較例Ｎｏ．１０４は処理圧力が低いために抗折強度が低い。比較例Ｎｏ．１０６は保持時間が短いために抗折強度が低い。比較例Ｎｏ．１０８は保持時間が長いために抗折強度が低い。これに対し、本発明例Ｎｏ．１０１、１０３、１０５、１０７はいずれも本発明の条件を満たしていることから抗折強度の高いことが分かる。 As shown in Table 3, Comparative Example No. No. 102 has a low bending strength due to the low processing temperature. Comparative Example No. No. 104 has a low bending strength due to a low processing pressure. Comparative Example No. 106 has a low bending strength due to its short holding time. Comparative Example No. No. 108 has a low bending strength due to a long holding time. On the other hand, the present invention example No. Since 101, 103, 105 and 107 all satisfy the conditions of the present invention, it can be seen that the bending strength is high.
このように、高融点でかつモリブデンの中で熱力学的に安定な金属またはセラミックスからなる所定組成の添加粉末がモリブデン中で微細に、かつ、多数残留することから高温におけるモリブデンの結晶粒成長を抑制し、高強度な成形体を得ることが可能となり高耐熱部材の実用化を図ることが出来る極めて優れた効果を奏するものである。
特許出願人 山陽特殊製鋼株式会社
代理人 弁理士 椎 名 彊
In this way, the additive powder of a predetermined composition made of a metal or ceramic that has a high melting point and is thermodynamically stable in molybdenum remains minutely and in large numbers in the molybdenum, so that molybdenum crystal grains grow at high temperatures. Therefore, it is possible to obtain a molded article having a high strength, and it is possible to obtain a very excellent effect that a high heat-resistant member can be put into practical use.
Patent Applicant Sanyo Special Steel Co., Ltd.
Attorney Atsushi Shiina
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Cited By (13)
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|---|---|---|---|---|
| JP2010270345A (en) * | 2009-05-19 | 2010-12-02 | Toshiba Corp | Crucible made from molybdenum and method for manufacturing the same, and method for manufacturing sapphire single crystal |
| JP2011127150A (en) * | 2009-12-15 | 2011-06-30 | Toshiba Corp | Crucible made of tungsten molybdenum alloy, method for producing it and method for producing sapphire single crystal |
| JP2012107782A (en) * | 2010-11-15 | 2012-06-07 | Toshiba Corp | Crucible, manufacturing method of sapphire single crystal using the same, and manufacturing method of the crucible |
| CN103422040A (en) * | 2013-08-07 | 2013-12-04 | 金堆城钼业股份有限公司 | Preparation method of molybdenum and zirconium alloy wire |
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Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0885840A (en) * | 1994-09-19 | 1996-04-02 | Hiroaki Kurishita | Molybdenum alloy and production thereof |
| JP2000129389A (en) * | 1998-10-26 | 2000-05-09 | Tokyo Tungsten Co Ltd | Molybdenum sintered compact and its manufacture |
| JP2005307226A (en) * | 2004-04-16 | 2005-11-04 | Hitachi Metals Ltd | Mo BASED TARGET MATERIAL |
| JP2006299384A (en) * | 2005-04-25 | 2006-11-02 | Allied Material Corp | High heat-resistant molybdenum alloy and producing method therefor |
-
2010
- 2010-01-20 JP JP2010009635A patent/JP5546880B2/en not_active Expired - Fee Related
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0885840A (en) * | 1994-09-19 | 1996-04-02 | Hiroaki Kurishita | Molybdenum alloy and production thereof |
| JP2000129389A (en) * | 1998-10-26 | 2000-05-09 | Tokyo Tungsten Co Ltd | Molybdenum sintered compact and its manufacture |
| JP2005307226A (en) * | 2004-04-16 | 2005-11-04 | Hitachi Metals Ltd | Mo BASED TARGET MATERIAL |
| JP2006299384A (en) * | 2005-04-25 | 2006-11-02 | Allied Material Corp | High heat-resistant molybdenum alloy and producing method therefor |
Cited By (16)
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| JP2011127150A (en) * | 2009-12-15 | 2011-06-30 | Toshiba Corp | Crucible made of tungsten molybdenum alloy, method for producing it and method for producing sapphire single crystal |
| JP2012107782A (en) * | 2010-11-15 | 2012-06-07 | Toshiba Corp | Crucible, manufacturing method of sapphire single crystal using the same, and manufacturing method of the crucible |
| CN103422040B (en) * | 2013-08-07 | 2016-02-10 | 金堆城钼业股份有限公司 | A kind of preparation method of molybdenum zirconium alloy wire |
| CN103422040A (en) * | 2013-08-07 | 2013-12-04 | 金堆城钼业股份有限公司 | Preparation method of molybdenum and zirconium alloy wire |
| JP2017502166A (en) * | 2013-10-29 | 2017-01-19 | プランゼー エスエー | Sputtering target and manufacturing method thereof |
| JP2014224324A (en) * | 2014-07-09 | 2014-12-04 | 株式会社東芝 | Crucible made of tungsten-molybdenum alloy, method for producing the same, and method for producing sapphire single crystal |
| CN104525948A (en) * | 2014-12-23 | 2015-04-22 | 金堆城钼业股份有限公司 | Preparation method for molybdenum alloy electrode |
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