JP2021038448A - High-strength Ir alloy - Google Patents
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- 229910000575 Ir alloy Inorganic materials 0.000 title claims abstract description 14
- 229910045601 alloy Inorganic materials 0.000 abstract description 30
- 239000000956 alloy Substances 0.000 abstract description 30
- 230000001590 oxidative effect Effects 0.000 abstract description 10
- 238000001953 recrystallisation Methods 0.000 abstract description 9
- 229910052707 ruthenium Inorganic materials 0.000 abstract description 9
- 229910052758 niobium Inorganic materials 0.000 abstract description 4
- 239000006104 solid solution Substances 0.000 abstract description 4
- 230000000694 effects Effects 0.000 abstract description 3
- 238000005096 rolling process Methods 0.000 abstract description 3
- 238000000034 method Methods 0.000 abstract description 2
- 238000005491 wire drawing Methods 0.000 abstract description 2
- 239000000243 solution Substances 0.000 abstract 1
- 238000012360 testing method Methods 0.000 description 19
- 230000003647 oxidation Effects 0.000 description 18
- 238000007254 oxidation reaction Methods 0.000 description 18
- 230000000052 comparative effect Effects 0.000 description 11
- 239000010948 rhodium Substances 0.000 description 11
- 239000000463 material Substances 0.000 description 9
- 239000000843 powder Substances 0.000 description 6
- 229910052703 rhodium Inorganic materials 0.000 description 6
- 239000003779 heat-resistant material Substances 0.000 description 3
- 238000002844 melting Methods 0.000 description 3
- 230000008018 melting Effects 0.000 description 3
- BASFCYQUMIYNBI-UHFFFAOYSA-N platinum Chemical group [Pt] BASFCYQUMIYNBI-UHFFFAOYSA-N 0.000 description 3
- 238000012545 processing Methods 0.000 description 3
- 239000013078 crystal Substances 0.000 description 2
- 238000004090 dissolution Methods 0.000 description 2
- 238000011156 evaluation Methods 0.000 description 2
- 229910052741 iridium Inorganic materials 0.000 description 2
- GKOZUEZYRPOHIO-UHFFFAOYSA-N iridium atom Chemical compound [Ir] GKOZUEZYRPOHIO-UHFFFAOYSA-N 0.000 description 2
- 238000003754 machining Methods 0.000 description 2
- 239000011812 mixed powder Substances 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 229910052750 molybdenum Inorganic materials 0.000 description 2
- 238000003672 processing method Methods 0.000 description 2
- 239000007787 solid Substances 0.000 description 2
- 230000002195 synergetic effect Effects 0.000 description 2
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 1
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 1
- KJTLSVCANCCWHF-UHFFFAOYSA-N Ruthenium Chemical compound [Ru] KJTLSVCANCCWHF-UHFFFAOYSA-N 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 239000011651 chromium Substances 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 238000011978 dissolution method Methods 0.000 description 1
- 238000005530 etching Methods 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 238000005098 hot rolling Methods 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 239000011733 molybdenum Substances 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 229910052697 platinum Inorganic materials 0.000 description 1
- 238000002360 preparation method Methods 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 239000003870 refractory metal Substances 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 229910052702 rhenium Inorganic materials 0.000 description 1
- WUAPFZMCVAUBPE-UHFFFAOYSA-N rhenium atom Chemical compound [Re] WUAPFZMCVAUBPE-UHFFFAOYSA-N 0.000 description 1
- MHOVAHRLVXNVSD-UHFFFAOYSA-N rhodium atom Chemical compound [Rh] MHOVAHRLVXNVSD-UHFFFAOYSA-N 0.000 description 1
- 229910052721 tungsten Inorganic materials 0.000 description 1
- 229910052720 vanadium Inorganic materials 0.000 description 1
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 description 1
- 238000003466 welding Methods 0.000 description 1
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Abstract
Description
本発明は、高温強度に優れるＩｒ合金に関する。 The present invention relates to an Ir alloy having excellent high temperature strength.
白金族元素であるＩｒは、融点が高く、酸化による消耗も少ないことから、優れた高温材料として、単結晶育成用るつぼ、耐熱器具、ガスタービンなどの広い分野で用いられている。一方で、Ｉｒの高温での耐酸化性は、ＷやＭｏなどの他の高融点金属に比べて優れるものの十分でなく、１０００℃以上の高温域では揮発性の酸化物を生じて徐々に消耗することが知られている。したがって、これまでの合金開発においては、主にその耐酸化性の改善に主眼が置かれてきた。 Ir, which is a platinum group element, has a high melting point and is less consumed by oxidation. Therefore, it is used as an excellent high-temperature material in a wide range of fields such as crucibles for growing single crystals, heat-resistant appliances, and gas turbines. On the other hand, the oxidation resistance of Ir at high temperatures is superior to that of other refractory metals such as W and Mo, but is not sufficient, and volatile oxides are generated and gradually consumed in the high temperature range of 1000 ° C. or higher. It is known to do. Therefore, in the development of alloys so far, the main focus has been on improving the oxidation resistance.
特許文献１には、耐熱材料であって、イリジウムをベースとし、第二元素としてロジウムを０．１〜３０ｗｔ％の範囲内で添加し、更に第三元素として白金、ルテニウム、レニウム、クロム、バナジウム、モリブデンこれらいずれか一種を０．１〜２０ｗｔ％の固溶範囲内で添加し、この第三元素と前記第二元素との添加総量が０．２〜５０ｗｔ％の固溶範囲内であることを特徴とするイリジウム基合金が開示されている。大気中１０５０℃における耐酸化性に優れていることが記載されている。 Patent Document 1 describes a heat-resistant material based on iridium, to which rhodium is added in the range of 0.1 to 30 wt% as the second element, and platinum, ruthenium, rhenium, chromium, and vanadium as the third element. , Molybdenum Any one of these is added within the solid dissolution range of 0.1 to 20 wt%, and the total amount of the third element added to the second element is within the solid dissolution range of 0.2 to 50 wt%. An iridium-based alloy characterized by the above is disclosed. It is described that it has excellent oxidation resistance at 1050 ° C. in the atmosphere.
ＩｒＲｈ合金は、高融点であり良好な耐酸化性を示すものの、機械的強度が十分ではない。例えば、るつぼやガスタービンなどに使用する場合、るつぼの内容物の膨張に耐えられなければならず、また、高速回転するタービンの遠心力に耐えられる機械的強度が必要である。よって、これらの分野では常に高い高温強度を有するＩｒ合金が求められている。 The IrRh alloy has a high melting point and exhibits good oxidation resistance, but its mechanical strength is not sufficient. For example, when used in a crucible or a gas turbine, it must be able to withstand the expansion of the contents of the crucible and must have mechanical strength to withstand the centrifugal force of a turbine rotating at high speed. Therefore, in these fields, Ir alloys having high high temperature strength are always required.
そこで、本発明の目的は、高温強度に優れるＩｒ合金を提供することである。 Therefore, an object of the present invention is to provide an Ir alloy having excellent high temperature strength.
ＩｒＲｈ合金の高温強度を向上させるための研究を鋭意重ねた結果、Ｒｕと少量のＮｂを同時に添加することで、高温強度に優れたＩｒ合金を開発するに至った。また、Ｉｒの一部に代えてＮｉを４ｍａｓｓ％以下含有させてもよい。 As a result of diligent research to improve the high temperature strength of the IrRh alloy, we have developed an Ir alloy having excellent high temperature strength by adding Ru and a small amount of Nb at the same time. Further, Ni may be contained in an amount of 4 mass% or less instead of a part of Ir.
本発明は、Ｒｈを５〜３５ｍａｓｓ％、Ｒｕを０．１〜２５ｍａｓｓ％、Ｎｂを０．１〜３ｍａｓｓ％、Ｎｉを０〜４ｍａｓｓ％含有し、残部がＩｒであることを特徴とするＩｒ合金である。 The present invention is an Ir alloy containing 5 to 35 mass% of Rh, 0.1 to 25 mass% of Ru, 0.1 to 3 mass% of Nb, 0 to 4 mass% of Ni, and the balance is Ir. Is.
本発明によれば、高温強度に優れたＩｒ合金を提供することができる。 According to the present invention, it is possible to provide an Ir alloy having excellent high temperature strength.
本発明は、Ｒｈを５〜３５ｍａｓｓ％、Ｒｕを０．１〜２５ｍａｓｓ％、Ｎｂを０．１〜３ｍａｓｓ％、Ｎｉを０〜４ｍａｓｓ％含有し、残部がＩｒであることを特徴とするＩｒ合金である。ここで、Ｎｉを０〜４ｍａｓｓ％含むとは、Ｎｉを含まないか、または４ｍａｓｓ％以下含むことを意味する。 The present invention is an Ir alloy containing 5 to 35 mass% of Rh, 0.1 to 25 mass% of Ru, 0.1 to 3 mass% of Nb, 0 to 4 mass% of Ni, and the balance is Ir. Is. Here, the term "containing 0 to 4 mass%" means that Ni is not contained or is contained in an amount of 4 mass% or less.
本発明のＩｒ合金は、合金を構成する全成分の中、Ｉｒを４０ｍａｓｓ％以上、好ましくは４５ｍａｓｓ％以上、より好ましくは５０ｍａｓｓ％以上、さらに好ましくは５５ｍａｓｓ％以上含有する。 The Ir alloy of the present invention contains Ir in an amount of 40 mass% or more, preferably 45 mass% or more, more preferably 50 mass% or more, still more preferably 55 mass% or more, among all the components constituting the alloy.
ＲｈとＲｕとの含有量の合計は５５ｍａｓｓ％以下が好ましい。ＲｈとＲｕとの含有量の合計は５０ｍａｓｓ％以下がより好ましい。ＲｈとＲｕとの含有量の合計は４５ｍａｓｓ％以下がさらに好ましい。 The total content of Rh and Ru is preferably 55 mass% or less. The total content of Rh and Ru is more preferably 50 mass% or less. The total content of Rh and Ru is more preferably 45 mass% or less.
Ｒｈの含有量が５ｍａｓｓ％を下回る場合には、Ｉｒ合金の耐酸化消耗性が不十分である。一方、Ｒｈの含有量が３５ｍａｓｓ％を超えると、Ｉｒ合金の耐酸化消耗性は良いが、融点及び再結晶温度が低下する。 When the Rh content is less than 5 mass%, the oxidation and wear resistance of the Ir alloy is insufficient. On the other hand, when the Rh content exceeds 35 mass%, the oxidative consumption resistance of the Ir alloy is good, but the melting point and the recrystallization temperature are lowered.
ＩｒＲｈ合金にＲｕを加えると、耐酸化消耗性が改善されるが、高温強度が不十分であった。 When Ru was added to the IrRh alloy, the oxidation wear resistance was improved, but the high temperature strength was insufficient.
Ｒｕに加えＮｂを上記含有量で添加することで、耐酸化消耗性を確保しつつＲｕとＮｂとの相乗的な固溶硬化を発現させ、高温強度が著しく向上した合金が得られる。Ｎｂの添加は合金の再結晶温度を上昇させ、高温での使用時の結晶成長を抑制する効果も発揮する。これにより加工組織を高温まで維持でき、耐熱材料として好適な高温強度の高い合金となる。 By adding Nb in addition to Ru at the above content, an alloy in which synergistic solid solution curing of Ru and Nb is exhibited while ensuring oxidation consumption resistance and high temperature strength is remarkably improved can be obtained. The addition of Nb raises the recrystallization temperature of the alloy and also exerts the effect of suppressing crystal growth during use at a high temperature. As a result, the processed structure can be maintained up to a high temperature, and an alloy having high high temperature strength suitable as a heat resistant material can be obtained.
Ｒｕの含有量が０．１ｍａｓｓ％を下回ると、耐酸化消耗性が低下する。また、Ｒｕの含有量が２５ｍａｓｓ％を超えると、塑性変形能が低下し、加工が困難になるだけでなく、耐酸化消耗性も低下する。Ｒｕの含有量は０．５ｍａｓｓ％以上が好ましい。Ｒｕの含有量は１ｍａｓｓ％以上がより好ましい。 When the Ru content is less than 0.1 mass%, the oxidation consumption resistance is lowered. Further, when the Ru content exceeds 25 mass%, not only the plastic deformability is lowered and the processing becomes difficult, but also the oxidation wear resistance is lowered. The Ru content is preferably 0.5 mass% or more. The Ru content is more preferably 1 mass% or more.
Ｎｂの含有量が０．１ｍａｓｓ％を下回るとＲｕとの相乗的な固溶硬化が少なく高温強度が不十分である。一方、Ｎｂの含有量が３ｍａｓｓ％を超えると塑性変形能が低下して加工が困難になるとともに、Ｎｂの酸化が顕著になり耐酸化消耗性が低下する。Ｎｂの含有量は２．５ｍａｓｓ％以下が好ましい。一方、Ｎｂの含有量は０．２ｍａｓｓ％以上が好ましい。さらに、Ｎｂの含有量は０．３ｍａｓｓ％以上がより好ましい。 When the Nb content is less than 0.1 mass%, the synergistic solid solution hardening with Ru is small and the high temperature strength is insufficient. On the other hand, when the content of Nb exceeds 3 mass%, the plastic deformability is lowered and the processing becomes difficult, and the oxidation of Nb becomes remarkable and the oxidation consumption resistance is lowered. The Nb content is preferably 2.5 mass% or less. On the other hand, the Nb content is preferably 0.2 mass% or more. Further, the Nb content is more preferably 0.3 mass% or more.
合金の強度を向上させる元素として、Ｎｉを４ｍａｓｓ％以下の範囲で添加してもよい。Ｎｉの含有量が４ｍａｓｓ％を超えると、Ｎｉの酸化消耗が顕著となり、耐酸化消耗性が低下する。Ｎｉの含有量は３．５ｍａｓｓ％以下が好ましい。一方、Ｎｉの含有量は０．１ｍａｓｓ％以上が好ましく、０．３ｍａｓｓ％以上がより好ましい。また、Ｎｉの含有量は０．５ｍａｓｓ％以上がさらに好ましい。 Ni may be added in the range of 4 mass% or less as an element for improving the strength of the alloy. When the Ni content exceeds 4 mass%, the oxidative consumption of Ni becomes remarkable, and the oxidative consumption resistance is lowered. The Ni content is preferably 3.5 mass% or less. On the other hand, the Ni content is preferably 0.1 mass% or more, more preferably 0.3 mass% or more. Further, the Ni content is more preferably 0.5 mass% or more.
上記の組成範囲の合金とすることで、単相の固溶体合金を得ることができる。そのため、本発明による合金は展延性を有し、圧延加工や伸線加工など、既知の加工法を用いて様々な形状を得ることができる。また、機械加工及び溶接などの加工方法も適用できる。 A single-phase solid solution alloy can be obtained by using an alloy having the above composition range. Therefore, the alloy according to the present invention has malleability, and various shapes can be obtained by using known processing methods such as rolling and wire drawing. Further, processing methods such as machining and welding can also be applied.
本発明の実施例について説明する。実施例及び比較例の合金の組成を表１に、試験結果を表２に示す。
まず、各原料粉末（Ｉｒ粉末、Ｒｈ粉末、Ｒｕ粉末、Ｎｂ粉末、Ｎｉ粉末）を所定の割合で混合し、混合粉末を作製した。次いで、得られた混合粉末を、一軸加圧成形機を用いて成形し圧粉体を得た。得られた圧粉体をアーク溶解法により溶解し、インゴットを作製した。
Examples of the present invention will be described. The composition of the alloys of Examples and Comparative Examples is shown in Table 1, and the test results are shown in Table 2.
First, each raw material powder (Ir powder, Rh powder, Ru powder, Nb powder, Ni powder) was mixed at a predetermined ratio to prepare a mixed powder. Next, the obtained mixed powder was molded using a uniaxial pressure molding machine to obtain a green compact. The obtained green compact was dissolved by an arc dissolution method to prepare an ingot.
次いで、作製したインゴットを熱間鍛造し、厚さ４ｍｍの板材とした。この板材を熱間圧延して厚さ１ｍｍの板材とした。高温強度測定の試験片作成に対しては、さらに厚さ０．６ｍｍになるよう熱間圧延した。 Next, the produced ingot was hot forged to obtain a plate material having a thickness of 4 mm. This plate material was hot-rolled to obtain a plate material having a thickness of 1 mm. For the preparation of test pieces for high-temperature strength measurement, hot rolling was performed so that the thickness was further 0.6 mm.
加工性は、インゴットから圧延までの上記加工工程にて評価した。厚さ０．６ｍｍの板材が得られたものを○、途中で割れが発生して厚さ０．６ｍｍの板材が得られなかったものを×として表２に示した。 The workability was evaluated in the above processing steps from ingot to rolling. Table 2 shows those in which a plate material having a thickness of 0.6 mm was obtained as ◯, and those in which a plate material having a thickness of 0.6 mm was not obtained due to cracking in the middle as ×.
耐酸化消耗性の評価は、厚さ１ｍｍの板材から円柱状に切り出した各試験片を用いて高温酸化試験により行った。高温酸化試験は、電気炉内に試験片をセットし、大気中、１２００℃の条件で２０時間保持した。耐酸化消耗性は、前記高温酸化試験における質量変化と定義した。質量変化ΔＭ（ｍｇ／ｍｍ2）は、試験片の試験前の質量をＭ０（ｍｇ）、試験後の質量をＭ１（ｍｇ）、試験片の試験前の表面積をＳ（ｍｍ2）とし、ΔＭ＝（Ｍ１−Ｍ０）／Ｓの式から求めた。また、試験片の表面積Ｓ（ｍｍ2）は、試験片の寸法から算出した。 The oxidative wear resistance was evaluated by a high-temperature oxidation test using each test piece cut out in a columnar shape from a plate material having a thickness of 1 mm. In the high temperature oxidation test, a test piece was set in an electric furnace and kept in the air at 1200 ° C. for 20 hours. Oxidation and wear resistance was defined as the mass change in the high temperature oxidation test. For the mass change ΔM (mg / mm 2 ), the mass of the test piece before the test is M0 (mg), the mass after the test is M1 (mg), and the surface area of the test piece before the test is S (mm 2 ). = (M1-M0) / S. The surface area S (mm 2 ) of the test piece was calculated from the dimensions of the test piece.
１２００℃での耐酸化消耗性の評価は、質量変化ΔＭが−０．０５までの合金は耐酸化消耗性が特に良好（酸化消耗量が少ない）とし、表２に記号Ａで示した。質量変化ΔＭが−０．０５未満、−０．２０以上の合金は耐酸化消耗性が良好とし、表２に記号Ｂで示した。質量変化ΔＭが−０．２０未満の合金は耐酸化消耗性が悪い（酸化消耗量が多い）とし、表２に記号Ｃで示した。 In the evaluation of the oxidative consumption resistance at 1200 ° C., the alloy having a mass change ΔM up to −0.05 was considered to have particularly good oxidative consumption resistance (small oxidative consumption), and is indicated by the symbol A in Table 2. Alloys having a mass change ΔM of less than −0.05 and −0.20 or more are considered to have good oxidation and wear resistance, and are indicated by the symbol B in Table 2. Alloys with a mass change ΔM of less than −0.20 are considered to have poor oxidative consumption resistance (large oxidative consumption), and are indicated by the symbol C in Table 2.
再結晶温度は、試験片をＡｒ雰囲気の電気炉中で９５０℃、１０００℃、１０５０℃、１１００℃、１１５０℃、１２００℃にて３０ｍｉｎ処理し、その試験片の断面を研磨し、研磨面をエッチングして金属顕微鏡（倍率２００倍）で組織観察して決定した。一つの試験片について一つの温度で熱処理した。 As for the recrystallization temperature, the test piece was treated in an electric furnace in an Ar atmosphere at 950 ° C, 1000 ° C, 1050 ° C, 1100 ° C, 1150 ° C, and 1200 ° C for 30 minutes, the cross section of the test piece was polished, and the polished surface was polished. It was determined by etching and observing the structure with a metallurgical microscope (magnification 200 times). One test piece was heat-treated at one temperature.
組織観察の結果、再結晶粒が認められた試験片の熱処理温度をその合金の再結晶温度と定義した。例えば，１０５０℃で再結晶粒が認められず、１１００℃で再結晶粒が認められた場合、再結晶温度を１１００℃とした。再結晶温度の評価は、１１００℃以上の合金を表２に記号Ａ、１０００℃以上１１００℃未満を表２に記号Ｂ、１０００℃未満を表２に記号Ｃで示した。 As a result of microstructure observation, the heat treatment temperature of the test piece in which recrystallized grains were observed was defined as the recrystallization temperature of the alloy. For example, when no recrystallized grains were observed at 1050 ° C. and recrystallized grains were observed at 1100 ° C., the recrystallization temperature was set to 1100 ° C. The evaluation of the recrystallization temperature is shown by symbol A in Table 2 for alloys of 1100 ° C. or higher, symbol B in Table 2 for 1000 ° C. or higher and lower than 1100 ° C., and symbol C in Table 2 for lower than 1000 ° C.
図１は、実施例７の合金を、１１００℃にて３０ｍｉｎ熱処理した場合の組織写真、図２は、比較例１の合金を、図１と同一の条件で熱処理した場合の組織写真である。図に示すように、比較例１では再結晶化が起きているが、実施例７の合金は加工組織を維持していることが分かる。 FIG. 1 is a microstructure photograph when the alloy of Example 7 is heat-treated at 1100 ° C. for 30 minutes, and FIG. 2 is a microstructure photograph when the alloy of Comparative Example 1 is heat-treated under the same conditions as in FIG. As shown in the figure, although recrystallization has occurred in Comparative Example 1, it can be seen that the alloy of Example 7 maintains the processed structure.
高温強度は、添加元素の効果を明確にするため、Ｎｂを添加していないＩｒＲｈＲｕ合金の代表として比較例１を基準とし、以下の手順で評価した。０．６ｍｍ厚みの板材からワイヤ放電加工により平行部が□０．５×０．６、長さ３ｍｍとなるよう試験片を切り出し、温度１２００℃、大気中、クロスヘッドスピード５ｍｍ／ｍｉｎで引張強さを算出した。得られた比較例１の引張強さをＴ０、実施例の引張強さをＴｘ（ｘは実施例の番号）
とし、高温強度比Ｔ（％）を、Ｔ＝Ｔｘ／Ｔ０×１００の式から求め、表２に示した。ここで、高温強度に優れるとは、具体的には、上述する式に従って算出される高温強度比Ｔ（％）が、１３０以上、好ましくは１４０以上であることを意味する。
The high-temperature strength was evaluated by the following procedure with reference to Comparative Example 1 as a representative of the IrRhRu alloy to which Nb was not added in order to clarify the effect of the added element. A test piece was cut out from a plate material with a thickness of 0.6 mm so that the parallel part would be □ 0.5 × 0.6 and the length would be 3 mm by wire electric discharge machining. Was calculated. The obtained tensile strength of Comparative Example 1 is T0, and the tensile strength of Example is Tx (x is the number of Example).
The high temperature intensity ratio T (%) was calculated from the formula T = Tx / T0 × 100 and is shown in Table 2. Here, "excellent in high temperature strength" specifically means that the high temperature strength ratio T (%) calculated according to the above formula is 130 or more, preferably 140 or more.
表２に示す結果から、比較例であるＩｒＲｈＲｕ合金に比べ、ＲｕとＮｂを同時に添加した実施例は、高温強度が顕著に高くなることがわかる。具体的には、Ｒｈ、Ｒｕ濃度が同じである比較例１と実施例６及び実施例７とを比較すると、実施例６及び実施例７の高温強度比Ｔ（％）は、それぞれ１９５と２２１であり、高温強度比が比較例１の１．９５倍及び２．２１倍と大きく向上している。また、Ｒｈ、Ｒｕ、Ｎｂ濃度が同じである実施例１と実施例２、実施例６と実施例１０を比較すると、高温強度比Ｔ（％）は、実施例１が１９７に対し実施例２が２３９、実施例６が１９５であるのに対し実施例１０が２２９であり、Ｎｉを添加することでＮｂのみを添加した場合よりも、更に高温強度が向上している。高温強度が向上している一方で、実施例の合金は再結晶温度及び耐酸化性は比較例１に劣らない特性を示している。このように、実施例の合金は耐熱材料として好ましい特性を有することが確認された。 From the results shown in Table 2, it can be seen that the high temperature strength of the example in which Ru and Nb are added at the same time is significantly higher than that of the IrRhRu alloy which is the comparative example. Specifically, when Comparative Example 1 and Example 6 and Example 7 having the same Rh and Ru concentrations are compared, the high-temperature intensity ratios T (%) of Examples 6 and 7 are 195 and 221 respectively. The high-temperature intensity ratio is significantly improved to 1.95 times and 2.21 times that of Comparative Example 1. Comparing Example 1 and Example 2 and Example 6 and Example 10 having the same Rh, Ru, and Nb concentrations, the high-temperature intensity ratio T (%) was found in Example 1 to 197 in Example 2. Is 239 and Example 6 is 195, whereas Example 10 is 229, and the addition of Ni further improves the high-temperature strength as compared with the case where only Nb is added. While the high-temperature strength is improved, the alloy of the example exhibits properties that are not inferior to those of Comparative Example 1 in recrystallization temperature and oxidation resistance. As described above, it was confirmed that the alloy of the example has preferable properties as a heat-resistant material.
また、実施例の合金は厚さ０．６ｍｍの板材にまで塑性加工ができたことから、比較例１と変わらない加工性を有することが示された。 Further, since the alloy of the example could be plastically worked to a plate material having a thickness of 0.6 mm, it was shown that the alloy had the same workability as that of Comparative Example 1.
Claims (1)
Ｒｕを０．１〜２５ｍａｓｓ％、
Ｎｂを０．１〜３ｍａｓｓ％、
Ｎｉを０〜４ｍａｓｓ％含有し、
残部がＩｒである、
ことを特徴とするＩｒ合金。 Rh 5 to 35 mass%,
Ru 0.1 to 25 mass%,
Nb 0.1 to 3 mass%,
Contains 0-4 mass% of Ni,
The rest is Ir,
An Ir alloy characterized by this.
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| JP2010517248A (en) * | 2007-01-31 | 2010-05-20 | ユラ・テック・カンパニー・リミテッド | Spark plug |
| JP2015159000A (en) * | 2014-02-24 | 2015-09-03 | 日本特殊陶業株式会社 | spark plug |
| WO2016189826A1 (en) * | 2015-05-28 | 2016-12-01 | 日本特殊陶業株式会社 | Sparkplug |
| WO2018021028A1 (en) * | 2016-07-25 | 2018-02-01 | 田中貴金属工業株式会社 | Spark plug electrode material |
| JP2021039911A (en) * | 2019-09-05 | 2021-03-11 | 日本特殊陶業株式会社 | Spark plug |
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| JP2010517248A (en) * | 2007-01-31 | 2010-05-20 | ユラ・テック・カンパニー・リミテッド | Spark plug |
| JP2015159000A (en) * | 2014-02-24 | 2015-09-03 | 日本特殊陶業株式会社 | spark plug |
| WO2016189826A1 (en) * | 2015-05-28 | 2016-12-01 | 日本特殊陶業株式会社 | Sparkplug |
| WO2018021028A1 (en) * | 2016-07-25 | 2018-02-01 | 田中貴金属工業株式会社 | Spark plug electrode material |
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