Patent Application
20190338395
The present invention relates to a heat-resistant Ir alloy.
Various alloys have been developed as heat-resistant materials to be used for a crucible for high temperature, a heat-resistant device, a gas turbine, a spark plug, a sensor for high temperature, a j et engine, and the like. As major heat-resistant materials, there are given, for example, heat-resistant steel, a nickel-based superalloy, a platinum alloy, and tungsten. The heat-resistant steel, the nickel-based superalloy, the platinum alloy, and the like have solidus points of less than 2,000° C., and hence cannot be used at a temperature of 2,000° C. or more. Meanwhile, high-melting point metals, such as tungsten and molybdenum, suffer from severe oxidation wear in the air at high temperature. In view of the foregoing, an Ir alloy has been developed as a heat-resistant material having a high melting point and having high oxidation wear resistance.
In Patent Literature 1, there is disclosed an Ir—Rh alloy to be used for a noble metal chip of a spark plug for an internal combustion engine in which 3 wt % to 30 wt % of Rh is added in order to prevent volatilization of Ir at high temperature. There is described that, when such alloy is employed, a chip which is excellent in heat resistance at high temperature and improved in wear resistance is obtained.
[PTL 1] JP 09-007733 A
The Ir alloy to be used as the heat-resistant material is required to be further increased in high temperature strength while ensuring oxidation wear resistance at high temperature.
Thus, an object of the present invention is to provide an Ir alloy which is excellent in high temperature strength while ensuring oxidation wear resistance at high temperature.
According to one embodiment of the present invention, there is provided a heat-resistant Ir alloy, including:
5 mass % to 30 mass % of Rh;
0.3 mass % to 5 mass % of an element group A consisting of at least one kind of element selected from among Ta and Re; and
0 mass % to 5 mass % of an element group B consisting of at least one kind of element selected from among Cr, Ni, and Co, wherein the heat-resistant Ir alloy includes 5 mass % or less of the element group A and the element group B in total, and wherein, when the at least one kind of element in the element group A includes Re alone, the at least one kind of element in the element group B is Co alone, Cr alone, or two or more kinds selected from Co, Cr, and Ni.
According to the present invention, the Ir alloy which is excellent in high temperature strength while ensuring oxidation wear resistance at high temperature can be provided.
The present invention is directed to a heat-resistant Ir alloy, including:
5 mass % to 30 mass % of Rh;
0.3 mass % to 5 mass % of an element group A consisting of at least one kind of element selected from among Ta and Re; and
0 mass % to 5 mass % of an element group B consisting of at least one kind of element selected from among Cr, Ni, and Co.
The heat-resistant Ir alloy includes 5 mass % or less of the element group A and the element group B in total.
When the element belonging to the element group A is Re, the element belonging to the element group B is Co alone or Cr alone, or two or more of Co, Cr and Ni.
The present invention is more specifically directed to a heat-resistant Ir alloy, including:
5 mass % to 30 mass % of Rh;
0.3 mass % to 5 mass % of Ta; and
0 mass % to 5 mass % of an element group B consisting of at least one kind of element selected from among Co, Cr, and Ni.
The heat-resistant Ir alloy includes 5 mass % or less of Ta and the element group B in total.
Herein, the above-mentioned “including 0 mass % to 5 mass % of an element group B consisting of at least one kind of element selected from among Co, Cr, and Ni” means that the heat-resistant Ir alloy may include 5 mass % or less of the element group B consisting of at least one selected from among Co, Cr, and Ni, or may not include the element group B. The content of Ta in the heat-resistant Ir alloy is preferably 0.5 mass % or more, and is more preferably 0.7 mass % or more.
The present invention is also specifically directed to a heat-resistant Ir alloy, including:
5 mass % to 30 mass % of Rh;
0.3 mass % to 5 mass % of an element group A consisting of Ta and Re in total; and
0 mass % to 5 mass % of an element group B consisting of at least one kind of element selected from among Co, Cr, and Ni.
The heat-resistant Ir alloy includes 5 mass % or less of the element group A and the element group B in total. Herein, the above-mentioned “including 0 mass % to 5 mass % of an element group B consisting of at least one kind of element selected from among Co, Cr, and Ni” means that the heat-resistant Ir alloy may include 5 mass % or less as of the element group B consisting of at least one kind of element selected from among Co, Cr, and Ni, or may not include the element group B. The content of the element group A is preferably 0.5 mass % or more, and is more preferably 0.7 mass % or more.
The present invention is also specifically directed to a heat-resistant Ir alloy, including:
5 mass % to 30 mass % of Rh;
0.3 mass % to 5 mass % of Re; and
0.1 mass % to 4.7 mass % of an element group B consisting of Co alone or Cr alone, or two or more kinds selected from among Co, Cr, and Ni.
When the element group B is consists of two or more kinds selected from among Co, Cr, and Ni, the heat-resistant Ir alloy includes 0.1 mass % to 4.7 mass % of the two or more kinds in total.
The heat-resistant Ir alloy includes 5 mass % or less of Re and the element group B in total.
When the Ir alloy includes 5 mass % to 30 mass % of Rh, oxidative volatilization of Ir from a crystal grain boundary is suppressed in the air at high temperature or in an oxidizing atmosphere, and the oxidation wear resistance of the alloy is remarkably improved. When the content of Rh is less than 5 mass %, the oxidation wear resistance of the Ir alloy is insufficient. Meanwhile, when the content of Rh is more than 30 mass %, the oxidation wear resistance of the Ir alloy is satisfactory, but the melting point and the recrystallization temperature of the Ir alloy are reduced.
When an Ir—Rh alloy includes 0.3 mass % to 5 mass % of the element group A, the strength of the alloy is increased through solid solution hardening due to the element group A. In addition, such Ir—Rh alloy is also increased in recrystallization temperature, and hence softening at high temperature is suppressed. When Ta is included alone or both Ta and Re are included as the element group A, high increasing effects on the high temperature strength and the recrystallization temperature of the alloy are obtained as compared to a case in which Re is included alone as the element group A. A composite oxide film between Ta and Rh is formed in the air at around 1,000° C., with the result that the oxidation wear resistance of the alloy is improved. When the content of the element group A is less than 0.3 mass %, the strength of the Ir—Rh alloy is insufficient owing to reduction in solid solution hardening. Meanwhile, when the content of the element group A is more than 5 mass %, the strength of the Ir—Rh alloy is further increased, but it becomes difficult to process the Ir—Rh alloy owing to reduction in plastic deformability. Besides, the element group A is oxidized remarkably, and the oxidation wear resistance is reduced. The content of the element group A is preferably 0.5 mass % or more, and is more preferably 0.7 mass % or more.
When an Ir—Rh-A alloy includes 5 mass % or less of the element group B, the strength of the alloy is further increased through solid solution hardening due to the element group B. In addition, in the air at high temperature (e.g., 1,200° C. or more) or in an oxidizing atmosphere, the element group B is oxidized, and the resultant oxide is distributed in a grain boundary. With this, outward diffusion of Ir and subsequent oxidative volatilization of Ir are suppressed, and thus the oxidation wear resistance of the alloy can be improved. When the content of the element group B is more than 5 mass %, the oxide of the element group B is excessively formed, and the oxidation wear resistance is reduced contrarily. In addition, also the melting point of the alloy is reduced. The content of the element group B is preferably 0.3 mass % or more.
Each of the above-mentioned alloys is formed of a single-phase solid solution which is free of a second phase. Therefore, each of the alloys has satisfactory ductility, can be plastically formed into various shapes and dimensions through known warm working or hot working, and is also easily mechanically processed or welded.
Examples of the present invention are described. The compositions of alloys of Examples and Comparative Examples are shown in Table 1, and the test results are shown in Table 2.
First, raw material powders (Ir powder, Rh powder, Ta powder, Re powder, Cr powder, Ni powder, and Co powder) were mixed at a predetermined ratio to produce mixed powder. Next, the resultant mixed powder was molded with a uniaxial pressing machine to provide a green compact. The resultant green compact was melted by an arc melting method to produce an ingot.
Next, the ingot thus produced was subjected to hot forging at 1,500° C. or more to provide a square bar having a width of 15 mm. The square bar was subjected to groove rolling at from 1,000° C. to 1,400° C., swaging processing, and wire drawing die processing to provide a wire rod of 0.5 mm.
The processability was evaluated through the above-mentioned step of processing the ingot into the wire rod. A case in which a wire rod of 0.5 mm was obtained was indicated by Symbol “∘”, and a case in which breakage occurred in the course of the processing and the wire rod was not obtained was indicated by Symbol “x”.
The oxidation wear resistance was evaluated by a high-temperature oxidation test using each test piece cut out of the wire rod into a length of 0.8 mm. The high-temperature oxidation test was performed by setting the test piece in an electric furnace, and retaining the test piece in the air under the conditions of 1,000° C. or 1,200° C. for 20 hours. The oxidation wear resistance was defined as a mass change through the high-temperature oxidation test. A mass change ΔM (mg/mm2) was determined by the following equation: ΔM=(M1−M0)/S, where M0 represents the mass (mg) of the test piece before the test, M1 represents the mass (mg) of the test piece after the test, and S represents the surface area (mm2) of the test piece before the test. In addition, the surface area S (mm2) of the test piece was calculated from the dimensions of the test piece.
Considering that Ir had a characteristic of being liable to suffer from oxidation wear at around 1,000° C., the evaluation of the oxidation wear resistance was performed at 1,000° C., and was also performed as 1,200° C. in order to evaluate the oxidation wear resistance at higher temperature.
The evaluation of the oxidation wear resistance at 1,000° C. was performed as described below. An alloy having a value for ΔM of −0.10 or more was evaluated as having particularly satisfactory oxidation wear resistance (having a small oxidation wear amount), and was indicated by Symbol “∘∘” in Table 2. An alloy having a value for ΔM of less than −0.10 and −0.25 or more was evaluated as having satisfactory oxidation wear resistance, and was indicated by Symbol “∘” in Table 2. An alloy having a value for ΔM of less than −0.25 was evaluated as having poor oxidation wear resistance (having a large oxidation wear amount), and was indicated by Symbol “x” in Table 2.
The evaluation of the oxidation wear resistance at 1,200° C. was performed as described below. An alloy having a value for ΔM of −0.20 or more was evaluated as having particularly satisfactory oxidation wear resistance (i.e., having a small oxidation wear amount), and was indicated by Symbol “∘∘” in Table 2. An alloy having a value for ΔM of less than −0.20 and −0.35 or more was evaluated as having satisfactory oxidation wear resistance, and was indicated by Symbol “∘” in Table 2. An alloy having a value for ΔM of less than −0.35 was evaluated as having poor oxidation wear resistance (having a large oxidation wear amount), and was indicated by Symbol “x” in Table 2.
The solidus point was evaluated by increasing the temperature of each test piece up to 2,100° C. in an electric furnace in an Ar atmosphere, and observing the appearance and the sectional surface of the test piece. The sectional surface was polished, and the polished surface was subjected to Ar ion etching and then observed with a metallographic microscope (at a magnification of 100 times). A case in which no change was observed in the appearance and on the sectional surface was evaluated as having a solidus point of 2,100° C. or more (indicated by Symbol “∘” in Table 2), and a case in which a melting mark was observed in the appearance or on the sectional surface was evaluated as having a solidus point of less than 2,100° C. (indicated by Symbol “x” in Table 2).
The recrystallization temperature was determined as described below. Each test piece was subjected to treatment at 1,000° C., 1,050° C., 1,100° C., 1,150° C., 1,200° C., 1,250° C., or 1,300° C. for 30 min in an electric furnace in an Ar atmosphere. A sectional surface of the test piece was polished, and the polished surface was subjected to Ar ion etching, and to structure observation with a metallographic microscope (at a magnification of 100 times). One test piece was subjected to heat treatment at one temperature.
As a result of the structure observation, a heat treatment temperature of the test piece at which a recrystallized grain was observed was defined as the recrystallization temperature of the alloy. For example, as shown in
The high temperature strength was evaluated by determining tensile strength by a tensile test at high temperature. As a test piece, a wire rod measuring φ0.5×150 mm was used after annealing at 1,500° C. The conditions of the tensile test were as follows: at a temperature of 1,200° C., in the air, and at a crosshead speed of 10 mm/min. The high temperature strength was evaluated as follows: a case of having a tensile strength of 200 MPa or less was indicated by Symbol “A” in Table 2, a case of having a tensile strength of more than 200 MPa and 400 MPa or less was indicated by Symbol “∘” in Table 2, and a case of having a tensile strength of more than 400 MPa was indicated by Symbol “∘∘” in Table 2.
The overall evaluation was performed as described below. In each of the items of the oxidation wear resistance at 1,000° C. and 1,200° C., the recrystallization temperature, and the high temperature strength, Symbol “00” had a score of 3 points, Symbol “∘” had a score of 2 points, Symbol “A” had a score of 1 point, and Symbol “x” had a score of 0 points. A case of having a total score of 12 points was indicated by Symbol “A”, a case of having a total score of from 8 points to 11 points was indicated by Symbol “B”, and a case of having a total score of 7 points or less was indicated by Symbol “C”. A case in which the processability or the solidus point was evaluated as poor (indicated by Symbol “x” in Table 2) was indicated by Symbol “D”.
From the results shown in Table 2, it was confirmed that the alloys of Examples each had satisfactory oxidation resistance, and had a high solidus point, a high recrystallization temperature, and excellent high temperature strength, and thus had particularly preferred characteristics as a heat-resistant material.
From the fact that the oxidation wear resistance at 1,000° C. is evaluated as particularly satisfactory (indicated by Symbol “00” in Table 2) in each of Examples 11 and 21 and the oxidation wear resistance at 1,000° C. is evaluated as satisfactory (indicated by Symbol “∘” in Table 2) in each of Examples 22 and 23, it is revealed that the oxidation wear resistance at 1,000° C. becomes more satisfactory in the case of the addition of Ta than in the case of the addition of Re. In addition, through comparison between Example 11 and Example 22 and between Example 21 and Example 23, it is revealed that the recrystallization temperature and the high temperature strength become higher in the case of the addition of Ta than in the case of the addition of Re.
An effect exhibited by the addition of the element group B is considered. For example, through comparison between Example 7 and Example 11, it is revealed that the high temperature strength is increased by the addition of Cr. In addition, for example, through comparison among Example 6, Example 16, and Example 17, it is revealed that the high temperature strength is increased by the addition of Ni. In addition, for example, through comparison between Example 7 and Example 21, it is revealed that the high temperature strength is increased by the addition of Co.
In addition, the alloys of Examples were each able to be plastically formed even into a thin wire of φ0.5 mm, and it was indicated that products having various shapes were able to be easily obtained therefrom.
| Number | Date | Country | Kind |
|---|---|---|---|
| 2016-249860 | Dec 2016 | JP | national |
| 2017-242366 | Dec 2017 | JP | national |
| Filing Document | Filing Date | Country | Kind |
|---|---|---|---|
| PCT/JP2017/045632 | 12/20/2017 | WO | 00 |
