WO2015146931A1 - NiIr基耐熱合金及びその製造方法 - Google Patents
NiIr基耐熱合金及びその製造方法 Download PDFInfo
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- WO2015146931A1 WO2015146931A1 PCT/JP2015/058785 JP2015058785W WO2015146931A1 WO 2015146931 A1 WO2015146931 A1 WO 2015146931A1 JP 2015058785 W JP2015058785 W JP 2015058785W WO 2015146931 A1 WO2015146931 A1 WO 2015146931A1
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/10—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of nickel or cobalt or alloys based thereon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
- C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
- C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
- C22C19/055—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 20% but less than 30%
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
- C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
- C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
- C22C19/056—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 10% but less than 20%
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
- C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
- C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
- C22C19/057—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being less 10%
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C30/00—Alloys containing less than 50% by weight of each constituent
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- the present invention relates to a NiIr-based heat-resistant alloy made of a Ni—Ir—Al—W alloy and a method for producing the same. More specifically, the present invention relates to a NiIr-based heat-resistant alloy that has high strength and wear resistance even when exposed to harsh usage environments, and a method for producing the same.
- NiIr-based heat-resistant alloy is an alloy in which Ir, Al, and W, which are essential additive elements, are added to Ni, and Ir: 5.0 to 50.0 mass%, Al: 1.0 to 8. It has a composition of 0% by mass, W: 5.0-20.0% by mass, and the balance Ni.
- the above novel NiIr-base heat-resistant alloy is to utilize the precipitation strengthening effect of an intermetallic compound having an L1 2 structure is gamma 'phase as a strengthening mechanism ((Ni, Ir) 3 ( Al, W)) . Since the ⁇ ′ phase exhibits reverse temperature dependence that increases in strength as the temperature rises, it can impart excellent high temperature strength and high temperature creep properties to the alloy.
- the utilization of the strengthening action by the ⁇ ′ phase is the same as the conventionally known strengthening mechanism of the Ni-base heat-resistant alloy, but the NiIr-base heat-resistant alloy by the applicant of the present application is the behavior of the ⁇ ′ phase at high temperatures. Is improved and the high temperature stability is better than that of the Ni-base heat-resistant alloy.
- an alloy is manufactured mainly by a process of manufacturing an alloy ingot having a target composition by a melt casting method, and an alloy product is manufactured by adding an appropriate thermomechanical process.
- the NiIr-based heat-resistant alloy by the applicant of the present application can also be manufactured by a general melt casting method, and further, an aging heat treatment is performed for precipitation of the ⁇ 'phase, which is the main strengthening mechanism.
- the aging heat treatment is preferably performed at a temperature range of 700 to 1300 ° C. for 0.5 minutes to 72 hours.
- the above-mentioned NiIr-based heat-resistant alloy suppresses the generation of the third phase (B2 phase) that causes embrittlement by making the composition range appropriate, and has excellent strength at high temperatures. It has been confirmed that it exhibits wear resistance. However, unpredictable wear has been observed for products obtained with several alloy samples. Such characteristic defects in NiIr-based heat-resistant alloys do not always occur but must be avoided.
- the present invention clarifies the cause of the accidental characteristic failure that occurs in the NiIr-based heat-resistant alloy by the applicant of the present application, and provides an alloy in which strength, hardness, and wear resistance at high temperatures are ensured. And the method of enabling manufacture of such a NiIr base heat-resistant alloy stably is also specified.
- the present inventors first examined factors that cause the above-described characteristic defects in the NiIr-based heat-resistant alloys of the present inventors. As a result, it has been found that a material that causes high temperature consumption has a difference in the phase structure of the alloy as compared with a material that does not cause a problem. This point will be described in detail.
- the ⁇ ′ phase ((Ni, Ir) 3 (Al, W)) is a main phase for ensuring the high-temperature strength of the alloy.
- the Ir 3 W phase sometimes precipitates depending on the production conditions of the alloy, and such an alloy has been found to be inferior in high temperature characteristics. Therefore, the present inventors have conceived the present invention that a NiIr-based heat-resistant alloy having suitable high-temperature characteristics can be obtained by limiting the precipitation amount in consideration of the influence of the Ir 3 W phase.
- the heat-resistant alloy according to the present invention prescribes a NiIr-based heat-resistant alloy made of a Ni—Ir—Al—W-based alloy, and defines the amount of Ir 3 W phase that is presumed to be a cause of characteristic deterioration. It is.
- the present invention will be described in detail.
- the heat-resistant alloy according to the present invention contains Ni, Ir, Al, and W as essential constituent elements.
- Al which is an additive element, is a main constituent element of the ⁇ ′ phase and is a component necessary for the precipitation. If the Al content is less than 1.0% by mass, the ⁇ 'phase does not precipitate, or even if it precipitates, it does not contribute to the improvement of the high temperature strength. On the other hand, the proportion of the ⁇ ′ phase increases as the Al concentration increases, but when Al is added excessively, the proportion of the B2 type intermetallic compound (NiAl, hereinafter sometimes referred to as B2 phase) increases. Thus, it becomes brittle and lowers the strength of the alloy, so the upper limit of the Al content is set to 8.0% by mass. Al contributes to the improvement of the oxidation resistance of the alloy. Al is preferably 1.9 to 6.1% by mass.
- W is a component that contributes to the stabilization of the ⁇ ′ phase at high temperatures in the NiIr-based alloy, and is the main constituent element.
- NiIr-based alloys it is not known that the addition of W stabilizes the ⁇ 'phase, but according to the present inventors, the addition of W can increase the solid solution temperature of the ⁇ ' phase, Stability at high temperatures can be ensured.
- W is added in an amount of less than 5.0% by mass, the high-temperature stability of the ⁇ ′ phase is not sufficiently improved.
- excessive addition exceeding 20.0 mass% promotes the generation of a phase mainly composed of W having a large specific gravity, and segregation is likely to occur.
- W also has the effect of strengthening the alloy matrix by solid solution.
- W is preferably 10.0 to 20.0% by mass.
- Ir is dissolved in the matrix ( ⁇ phase) and partially substituted with ⁇ ′ phase Ni, thereby increasing the solidus temperature and the solid solution temperature for the ⁇ phase and ⁇ ′ phase, respectively, and heat resistance. It is an additive element that improves the properties. Ir exhibits an addition effect at 5.0% by mass or more, but excessive addition increases the specific gravity of the alloy, and the solidus temperature of the alloy becomes high, so the upper limit is 50.0% by mass. And Ir is preferably 10.0 to 45.0% by mass.
- the Ni-base heat-resistant alloy according to the present invention may contain an additional additive element for further improvement of the high temperature characteristics or additional characteristics.
- this additional additive element include B, Co, Cr, Ta, Nb, Ti, V, and Mo.
- B is an alloy component that segregates at the grain boundaries and strengthens the grain boundaries, and contributes to the improvement of high-temperature strength and ductility.
- the effect of addition of B becomes significant at 0.001% by mass or more, but excessive addition is not preferable for workability, so the upper limit is made 0.1% by mass.
- a preferable addition amount of B is 0.005 to 0.02 mass%.
- Co is effective in increasing the strength by increasing the proportion of the ⁇ 'phase. Co partially substitutes for Ni in the ⁇ 'phase and becomes a constituent element. Such an effect is seen with addition of 5.0% by mass or more of Co. However, excessive addition lowers the solid solution temperature of the ⁇ ′ phase, thereby impairing the high temperature characteristics. Therefore, it is preferable to make 20.0 mass% into the upper limit of Co content. Co also has an effect of improving the wear resistance.
- Cr is also effective for strengthening grain boundaries. Further, when Cr is added to the alloy, Cr strengthens the grain boundary by forming carbides and precipitating in the vicinity of the grain boundary. The effect of addition is seen when the amount of Cr added is 1.0% by mass or more. However, if added excessively, the melting point of the alloy and the solid solution temperature of the ⁇ 'phase are lowered, and the high temperature characteristics are impaired. Therefore, the addition amount of Cr is preferably 25.0% by mass or less. Note that Cr also has an action of forming a dense oxide film on the alloy surface and improving oxidation resistance.
- Ta is an element that stabilizes the ⁇ 'phase and is effective in improving the high temperature strength of the ⁇ phase by solid solution strengthening.
- carbide can be formed and precipitated, so that it is an effective additive element for grain boundary strengthening.
- Ta exhibits the said effect
- excessive addition causes generation
- Nb, Ti, V, and Mo are also effective additive elements for improving the high temperature strength by stabilizing the ⁇ ′ phase and strengthening the matrix by solid solution strengthening.
- Nb, Ti, V, and Mo are preferably added in an amount of 1.0 to 5.0% by mass.
- the additive elements of B, Co, Cr, Ta, Nb, Ti, V, and Mo improve the grain boundary strength by segregating in the vicinity of the grain boundary, and at the same time stabilize the ⁇ ′ phase. Strength can be improved.
- Co, Cr, Ta, Nb, Ti, V, and Mo also act as constituent elements of the ⁇ ′ phase.
- Gamma in this case 'the crystal structure of the phase, gamma additive elements is not Ni-Ir-Al-W4 binary alloy' has the same L1 2 structure and phase, (Ni, X) 3 ( Al, W, Z ).
- X is Ir and Co
- Z is Ta, Cr, Nb, Ti, V, and Mo.
- C can be cited as a more effective additive element.
- C improves the high temperature strength and ductility by forming a carbide together with the metal element in the alloy and precipitating. Such an effect is seen with 0.001 mass% or more of C addition, but excessive addition is not preferable for workability and toughness, so 0.5 mass% is made the upper limit of the C content.
- a preferable addition amount of C is 0.01 to 0.2% by mass.
- C has a great significance in the formation of carbides as described above, but in addition to this, C is an element effective for grain boundary strengthening by segregating in the same manner as B.
- the concentration of each alloy element is within the range described above, and a ⁇ ′ phase that functions as a strengthening phase is precipitated at a high temperature.
- the phase structure of the alloy according to the present invention will be described.
- the ⁇ ′ phase which is the main strengthening phase, is (Ni, Ir) 3 (Al, W).
- This precipitation strengthening action by the ⁇ ′ phase is the same as that of the conventional Ni-based alloy and Ir-based alloy.
- the ⁇ ′ phase has an inverse temperature dependence on strength, and therefore has high temperature stability. In the present invention, the high temperature stability of the ⁇ ′ phase is further improved.
- the particle diameter of the ⁇ ′ phase in the Ni-base heat-resistant alloy according to the present invention is preferably 10 nm to 1 ⁇ m.
- the precipitation strengthening action can be obtained with precipitates of 10 nm or more, but it decreases with coarse precipitates exceeding 1 ⁇ m.
- the present invention limits the amount of precipitation of Ir 3 W-phase which is believed to affect the high temperature properties of the alloy. Specifically, the ratio (Y / X) between the peak intensity (X) of the (111) plane of the ⁇ ′ phase and the peak intensity (Y) of the (201) plane of the Ir 3 W phase is 0.5 or less. To do.
- the reason why the present invention is based on the result of X-ray diffraction analysis is that although this analysis method is relatively simple, it shows a relatively appropriate result in defining the phase structure.
- the peak intensity ratio (Y / X) is preferably 0.1 or less, and most preferably 0.
- the NiIr-based alloy according to the present invention improves the high-temperature strength by appropriately dispersing the ⁇ ′ phase, but does not exclude the formation of other phases except for the Ir 3 W phase. That is, when Al, W, or Ir is added in the above range, depending on the composition, not only the ⁇ ′ phase but also the B2 phase may precipitate. Further, in this Ni—Al—W—Ir quaternary alloy, the ⁇ ′ phase having a D019 structure may also precipitate.
- the NiIr-based alloy according to the present invention ensures high-temperature strength even when precipitates other than these ⁇ ′ phases are present. However, precipitation of the B2 phase is relatively suppressed in the NiIr-based alloy according to the present invention.
- the NiIr-based alloy according to the present invention can stably exhibit a high hardness of 550 to 700 Hv (normal temperature).
- the manufacturing method of the NiIr-based alloy according to the present invention is basically in accordance with a general manufacturing method of an alloy, a step of manufacturing an alloy ingot having the above composition by a melt casting method, and a step of aging heat treatment of the alloy Is the main process.
- the NiIr-based alloy according to the present invention requires that the amount of precipitation of the Ir 3 W phase is not more than a certain amount in the material structure, and therefore, manufacturing conditions are set in consideration of this.
- the present inventors considered that it was due to the development mechanism of the cast structure (dendritic structure) related to the cooling rate in the manufacturing process of the alloy, particularly the melt casting process. .
- the dendrite structure is a structure that is always seen in the general melt casting process and is also called a dendritic crystal.
- the trunk part (primary arm) that is the main axis and branch parts (secondary arm and tertiary arm) that are generated from it. Composed. From such a form, in the dendrite structure, the primary arm is generated and grown to some extent, and then the secondary arm is generated and grown, and then the tertiary arm is sequentially generated.
- the microscopic morphology of the dendrite structure varies depending on the cooling rate. That is, when the cooling rate is fast, the primary arm is generated and grows rapidly, so the secondary and tertiary arms are generated almost simultaneously with the primary arm. As a result, the fine primary arm and the secondary and tertiary arms are densely packed.
- the present inventors can sufficiently precipitate the ⁇ ′ phase suitably even if the aging heat treatment for ⁇ ′ phase precipitation is performed thereafter in the region of the composition variation as described above. Therefore, it was considered that an undesirable precipitated phase such as an Ir 3 W phase was generated.
- the NiIr-based heat-resistant alloy of the present application is an alloy of a quaternary system or more containing a plurality of alloy elements.
- the ultra-high melting point metal of Ir and the low melting point metal of Al are included, the behavior during solidification cannot be completely controlled, and the influence of the thickness of the dendrite primary arm is estimated to be greater. Is done.
- the cooling rate in the casting process is set to 200 ° C./min or more.
- the cooling rate of less than 200 ° C. / min, the cooling can not promote the formation of secondary-tertiary arm growing a thick primary arm of the stem is too slow is mainly, precipitation amount of Ir 3 W-phase by composition variation Increase.
- the upper limit of the cooling rate is not set from the viewpoint of suppressing the precipitation of the Ir 3 W phase.
- an excessively high cooling rate gives an inappropriate solidification strain and causes cracking, so that it is preferably 500 ° C./min or less.
- a more preferable cooling rate is 300 ° C./min or more.
- the cooling rate in the casting process can be controlled by using a material having a high thermal conductivity (copper, silver, aluminum, or the like) as a constituent material of the mold and appropriately cooling the mold. Since the NiIr-based alloy according to the present invention has good castability and is difficult to crack during solidification, an alloy ingot can be manufactured in a state close to the final shape of the product to be manufactured at the stage of the casting process. (Near net shape). Therefore, it is possible to efficiently manufacture an alloy product by selecting a mold constituent material and optimizing the mold shape and dimensions.
- the manufacturing method of the NiIr-based alloy according to the present invention includes an aging heat treatment step after the melt casting step as an essential step. This is because the ⁇ ′ phase, which is a strengthening factor of the alloy, is precipitated by aging heat treatment.
- This aging heat treatment is performed in a temperature range of 700 to 1300 ° C. Preferably, the temperature range is 750 to 1200 ° C.
- the heating time at this time is preferably 30 minutes to 72 hours. In addition, you may perform this heat processing in multiple times, for example, heating at 1100 degreeC for 4 hours, and also heating at 900 degreeC for 24 hours.
- the cooling temperature after heating and holding at the above temperature in order to precipitate a fine ⁇ ′ phase and prevent material cracking, it is preferable to control the cooling temperature after heating and holding at the above temperature. If this cooling rate is too high, a coarse ⁇ 'phase may precipitate and affect the high temperature strength of the alloy. In addition, since the ⁇ 'phase may cause cracks due to thermal shock, the alloy may crack due to an excessively high cooling rate.
- the cooling rate after this aging heat treatment is preferably 5 to 80 ° C./sec.
- the NiIr-based alloy in which the ⁇ ′ phase is dispersed in the ⁇ phase is manufactured by the aging heat treatment.
- heat treatment for homogenization can be performed prior to aging heat treatment.
- an alloy manufactured by various methods is heated to a temperature range of 1100 to 1800 ° C.
- heating is performed in the range of 1200 to 1600 ° C.
- the heating time at this time is preferably 30 minutes to 72 hours.
- NiIr-based alloy according to the present invention can be cast with a near net shape, it can be formed into a final shape by slight processing after the casting process and the aging heat treatment process.
- the NiIr-based alloy according to the present invention can stably exhibit the inherent properties such as high-temperature strength and wear resistance.
- This NiIr-based alloy can be manufactured by appropriately setting the cooling rate in the melt casting process. Further, by adjusting the cooling rate after the aging heat treatment, an alloy having more preferable high temperature characteristics can be manufactured.
- FIG. 1 The measurement result of the tool dimension after the joining test by the FSW tool manufactured with the alloy which concerns on Example 1 and the comparative example 1.
- FIG. The figure which shows the change of the amount of wear with respect to the joining distance in a joining test.
- the photograph which shows the material structure after the melt casting of the alloy of Example 1 and Comparative Example 1.
- the photograph which shows the material structure of Example 1 and comparative example 1 after an aging heat processing.
- First Embodiment in this embodiment, as the NiIr-based heat-resistant alloy, 37.77 mass% Ni-25.0 mass% Ir-4.38 mass% Al-14.32 mass% W-7.65 mass% Co -4.67% by mass Ta-6.1% by mass Cr-0.1% by mass C-0.01% by mass B alloy is manufactured, processed into an FSW tool, and subjected to a bonding test. Abrasion was evaluated.
- a molten alloy was melted by arc melting in an inert gas atmosphere in the melting and casting process, poured into a mold, and cooled and solidified in the atmosphere.
- two types of molds were prepared: a copper mold having a space of the shape and dimension of the FSW tool as the final product and a ceramic mold used in the lost wax method. The dimensions of the mold are the same.
- the cooling rate in these molds is 450 ° C./min for the copper mold and 20 ° C./min for the ceramic mold.
- the alloy ingot produced by the melt casting process was subjected to a homogenization heat treatment at 1300 ° C. for 4 hours, heated for a predetermined time and then cooled.
- the cooling at this time was air cooling, but the cooling rate was 30 ° C./sec.
- the aging heat treatment was performed under the conditions of a temperature of 800 ° C. and a holding time of 24 hours, followed by heating for a predetermined time and then cooling.
- a convex FSW tool (dimensions: pin length 1.7 mm, shoulder diameter ⁇ 15 mm) was obtained by cutting after cooling.
- the tool was collected after one pass, the cross-sectional dimension was measured, and the wear amount (wear volume) of the most worn portion was measured.
- FIG. 1 An example of this measurement result is shown in FIG. 1, and the tool of Comparative Example 1 shows severe wear in the shoulder after joining.
- the tool of Example 1 shows slight wear at the shoulder as in Comparative Example 1, it can be said that the amount thereof is overwhelmingly small.
- FIG. 2 shows the change in the amount of wear with respect to the joining distance.
- the amount of wear significantly increases as the joining distance increases.
- Example 1 is less affected by the increase in the joining distance and the amount of wear is about 1/5 of the comparative example at the joining distance of 1800 mm (fourth pass).
- FIG. 3 shows the material structure after melt casting of Example 1 and Comparative Example 1. From this figure, the alloy ingot of Example 1 shows a structure in which the primary arm and secondary arm of the dendrite are finely packed. On the other hand, in Comparative Example 1, a thick primary arm is seen, but the secondary arm is insufficiently grown, and another solidified phase is seen between the dendrites. Further, FIG. 4 shows the material structures of Example 1 and Comparative Example 1 after aging heat treatment, and precipitation of the ⁇ ′ phase is observed in both materials, but in the comparative example, a portion with poor precipitation is observed.
- Example 1 and a comparative example are phase structures which differ greatly, and comparative example 1 has low abrasion resistance under high temperature.
- Second Embodiment Here, a NiIr-based heat-resistant alloy having the same composition as that of the first embodiment was manufactured by changing the cooling rate while changing the material of the mold, and the phase structure and metal structure were compared.
- a carbon mold and an iron mold (Comparative Example 2 and Comparative Example 3) were used as the mold. These molds have the same shape and dimensions.
- template (Example 2, comparative example 4) from which a dimension differs from 1st Embodiment was also used.
- the manufacturing process of the alloy in this embodiment is the same as that in the first embodiment, and only the cooling rate depending on the type of mold is different.
- X-ray diffraction analysis was performed to calculate the peak intensity ratio, and then a compressive strength test at 1000 ° C. was performed.
- Table 1 shows the calculated peak intensity ratio (Y / X) and the results of the compressive strength test at 1000 ° C.
- the compressive strength test at 1000 ° C. was conducted for Example 1 and Comparative Example 1 of the first embodiment, and Table 1 also shows the results.
- Comparative Examples 2 to 4 having a low cooling rate a peak due to the Ir 3 W phase occurs with a difference in strength, and the peak intensity ratio exceeds 0.5. And these alloys are inferior in compressive strength in 1000 degreeC. It can be confirmed that it is necessary to increase the cooling rate during casting as in Examples 1 and 2.
- the Ir 3 W phase may be slightly precipitated, so that in addition to the selection of the mold material, the cooling rate can be determined by appropriate heat capacity calculation or the like. Setting is required.
- the present invention is a NiIr-based alloy that can stably exhibit high-temperature strength, oxidation resistance, and wear resistance.
- the present invention is suitable for members such as a gas turbine, an airplane engine, a chemical plant, an automobile engine such as a turbocharger rotor, and a high temperature furnace.
- FSW friction stir welding
- Friction stir welding is a joining method in which a tool is pressed between materials to be joined and moved in the joining direction while rotating the tool at a high speed. This joining method joins the tool and the material to be joined by frictional heat and solid-phase stirring, and the tool becomes considerably hot.
- NiIr-based alloys can be used for joining relatively low melting point metals such as aluminum, but high melting point materials such as steel materials, titanium alloys, nickel-base alloys, zirconium-base alloys, etc. from the viewpoint of high-temperature strength.
- high melting point materials such as steel materials, titanium alloys, nickel-base alloys, zirconium-base alloys, etc. from the viewpoint of high-temperature strength.
- the NiIr-based alloy according to the present invention has improved high-temperature strength, it can be applied as a constituent material of a friction stir welding tool for joining the above-described high melting point materials.
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Abstract
Description
第1実施形態:本実施形態では、NiIr基耐熱合金として、37.77質量%Ni-25.0質量%Ir-4.38質量%Al-14.32質量%W-7.65質量%Co-4.67質量%Ta-6.1質量%Cr-0.1質量%C-0.01質量%B合金を製造し、これをFSWのツールに加工して接合試験を行い、合金の耐摩耗性を評価した。
・ツール挿入角度:3°
・挿入深さ:1.80mm/sec
・ツール回転速度:150rpm又は200rpm
・接合速度:1.00mm/sec
・シールドガス:アルゴン
・1パス当りの接合距離:250mm
Claims (7)
- Ir:5.0~50.0質量%、Al:1.0~8.0質量%、W:5.0~20.0質量%、残部NiのNi-Ir-Al-W系合金からなり、必須の強化相として、L12構造を有するγ’相がマトリックス中に析出・分散してなるNiIr基耐熱合金であって、
X線回折分析における、2θ=43°~45°の範囲で観察されるγ’相の(111)面のピーク強度(X)と、2θ=48°~50°の範囲で観察されるIr3W相の(201)面のピーク強度(Y)との比(Y/X)が、0.5以下であるNiIr基耐熱合金。 - 下記のグループIから選択される1種又は2種以上の添加元素を含む請求項1記載のNiIr基耐熱合金。
グループI:
B:0.001~0.1質量%、
Co:5.0~20.0質量%、
Cr:1.0~25.0質量%、
Ta:1.0~10.0質量%、
Nb:1.0~5.0質量%、
Ti:1.0~5.0質量%、
V:1.0~5.0質量%、
Mo:1.0~5.0質量% - 更に、0.001~0.5質量%のCを含み、炭化物が析出・分散する請求項1又は請求項2記載のNiIr基耐熱合金。
- 合金中のIrに対して、30質量%以下のRh又はPtを置換してなる請求項1~請求項3のいずれかに記載のNiIr基耐熱合金。
- 溶解鋳造法により請求項1~請求項4のいずれかに記載の組成を有する合金インゴットを製造する溶解鋳造工程と、700~1300℃の温度域で時効熱処理する工程、を有するNiIr基耐熱合金の製造方法であって、
溶解鋳造工程における冷却速度を200℃/ min以上とするNiIr基耐熱合金の製造方法。 - 時効熱処理工程は、合金を700~1300℃の温度域で加熱した後、5~80℃/secの冷却速度で冷却するものである請求項5記載のNiIr基耐熱合金の製造方法。
- 時効熱処理前に、NiIr基合金を1100~1800℃の温度域で均質化熱処理する請求項5又は請求項6記載のNiIr基耐熱合金の製造方法。
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EP15768897.9A EP3124630B1 (en) | 2014-03-28 | 2015-03-23 | Ni-ir-based heat-resistant alloy and process for producing same |
CN201580016770.8A CN106164307B (zh) | 2014-03-28 | 2015-03-23 | NiIr基耐热合金及其制造方法 |
US15/127,348 US10094012B2 (en) | 2014-03-28 | 2015-03-23 | Ni-Ir-based heat-resistant alloy and process for producing same |
KR1020167026869A KR101832654B1 (ko) | 2014-03-28 | 2015-03-23 | NiIr기 내열 합금 및 그 제조 방법 |
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JP2014067445A JP2015189999A (ja) | 2014-03-28 | 2014-03-28 | NiIr基耐熱合金及びその製造方法 |
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Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2018116810A1 (ja) * | 2016-12-22 | 2018-06-28 | 株式会社東北テクノアーチ | Ni基耐熱合金 |
CN115976363A (zh) * | 2022-12-13 | 2023-04-18 | 昆明理工大学 | 一种复合抗氧化层铂基合金及其制备方法 |
Families Citing this family (5)
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---|---|---|---|---|
JP5721189B2 (ja) * | 2013-03-12 | 2015-05-20 | 株式会社 東北テクノアーチ | 耐熱性Ni基合金及びその製造方法 |
JP6425274B2 (ja) * | 2016-12-22 | 2018-11-21 | 株式会社 東北テクノアーチ | Ni基耐熱合金 |
CN107779719B (zh) * | 2017-12-15 | 2020-02-07 | 湖南科技大学 | 一种铱镍铁合金及其制备方法与应用 |
CN111681714B (zh) * | 2020-07-02 | 2023-06-20 | 兰州大学 | 一种在定向凝固包晶合金中生长非典型三次枝晶的方法 |
CN112553487B (zh) * | 2020-12-14 | 2021-11-26 | 昆明富尔诺林科技发展有限公司 | 一种具有良好高温耐久烧蚀性能的铱镍合金火花塞中心电极材料及其制备方法 |
Citations (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2001294959A (ja) * | 2000-04-17 | 2001-10-26 | Mitsubishi Heavy Ind Ltd | 単結晶Ni基耐熱合金およびタービン翼 |
JP2010132966A (ja) * | 2008-12-04 | 2010-06-17 | Mitsubishi Materials Corp | 高温強度を有するNi基耐熱合金およびこの合金からなるガスタービン翼鋳物 |
JP2011225930A (ja) * | 2010-04-20 | 2011-11-10 | National Institute For Materials Science | 耐熱コーティング材 |
JP5721189B2 (ja) * | 2013-03-12 | 2015-05-20 | 株式会社 東北テクノアーチ | 耐熱性Ni基合金及びその製造方法 |
Family Cites Families (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP1026269B1 (en) | 1999-02-02 | 2004-12-01 | Japan as represented by Director General of National Research Institute for Metals | High-melting superalloy and method of producing the same |
GB0216323D0 (en) * | 2002-07-13 | 2002-08-21 | Johnson Matthey Plc | Alloy |
SE528807C2 (sv) * | 2004-12-23 | 2007-02-20 | Siemens Ag | Komponent av en superlegering innehållande palladium för användning i en högtemperaturomgivning samt användning av palladium för motstånd mot väteförsprödning |
CN101248198B (zh) * | 2005-09-15 | 2010-06-16 | 独立行政法人科学技术振兴机构 | 高耐热性、高强度Co基合金及其制造方法 |
EP1983067A4 (en) * | 2006-02-09 | 2012-11-07 | Japan Science & Tech Agency | IRIDIUM BASED ALLOY WITH HIGH HEAT RESISTANCE AND HIGH STRENGTH AND MANUFACTURING METHOD THEREFOR |
JP2008248322A (ja) * | 2007-03-30 | 2008-10-16 | Ishifuku Metal Ind Co Ltd | 耐熱性Ir基合金 |
CN102206769A (zh) * | 2011-04-11 | 2011-10-05 | 昆明富尔诺林科技发展有限公司 | 一种铱合金材料及其应用 |
JP5226846B2 (ja) | 2011-11-04 | 2013-07-03 | 田中貴金属工業株式会社 | 高耐熱性、高強度Rh基合金及びその製造方法 |
-
2014
- 2014-03-28 JP JP2014067445A patent/JP2015189999A/ja active Pending
-
2015
- 2015-03-13 TW TW104108126A patent/TWI557233B/zh not_active IP Right Cessation
- 2015-03-23 US US15/127,348 patent/US10094012B2/en active Active
- 2015-03-23 WO PCT/JP2015/058785 patent/WO2015146931A1/ja active Application Filing
- 2015-03-23 KR KR1020167026869A patent/KR101832654B1/ko active IP Right Grant
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Patent Citations (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2001294959A (ja) * | 2000-04-17 | 2001-10-26 | Mitsubishi Heavy Ind Ltd | 単結晶Ni基耐熱合金およびタービン翼 |
JP2010132966A (ja) * | 2008-12-04 | 2010-06-17 | Mitsubishi Materials Corp | 高温強度を有するNi基耐熱合金およびこの合金からなるガスタービン翼鋳物 |
JP2011225930A (ja) * | 2010-04-20 | 2011-11-10 | National Institute For Materials Science | 耐熱コーティング材 |
JP5721189B2 (ja) * | 2013-03-12 | 2015-05-20 | 株式会社 東北テクノアーチ | 耐熱性Ni基合金及びその製造方法 |
Non-Patent Citations (1)
Title |
---|
C.ZHANG ET AL.: "Modeling of phase stability of the fcc phases in the Ni-Ir-Al system using the cluster/site approximation method coupling with first-principles calculations", ACTA MATERIALIA, vol. 56, 14 March 2008 (2008-03-14), pages 2576 - 2584, XP022699328 * |
Cited By (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2018116810A1 (ja) * | 2016-12-22 | 2018-06-28 | 株式会社東北テクノアーチ | Ni基耐熱合金 |
JP2018104729A (ja) * | 2016-12-22 | 2018-07-05 | 国立大学法人東北大学 | Ni基耐熱合金 |
EP3561093A4 (en) * | 2016-12-22 | 2019-12-25 | Tohoku Techno Arch Co., Ltd. | Ni-BASED HEAT RESISTANT ALLOY |
US11066728B2 (en) | 2016-12-22 | 2021-07-20 | Tohoku Techno Arch Co., Ltd. | Ni-based heat-resistant alloy |
CN115976363A (zh) * | 2022-12-13 | 2023-04-18 | 昆明理工大学 | 一种复合抗氧化层铂基合金及其制备方法 |
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TW201606090A (zh) | 2016-02-16 |
TWI557233B (zh) | 2016-11-11 |
KR20160127114A (ko) | 2016-11-02 |
KR101832654B1 (ko) | 2018-02-26 |
EP3124630A1 (en) | 2017-02-01 |
CN106164307B (zh) | 2018-01-23 |
EP3124630A4 (en) | 2017-11-29 |
US10094012B2 (en) | 2018-10-09 |
JP2015189999A (ja) | 2015-11-02 |
US20170130310A1 (en) | 2017-05-11 |
EP3124630B1 (en) | 2019-06-12 |
CN106164307A (zh) | 2016-11-23 |
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