TW200806801A - High-temperature resistant alloys with low contents of Co and Ni - Google Patents

Abstract

A high temperature resistant alloy with low contents of Co and Ni having a face-centered cubic (FCC) crystal structure formed by selecting a proper combination of elements using the design of multiple alloy, which is characterized by excellent ability of deformation, toughness and high-temp strength. Such alloys are so configured that 5 to 7 principal elements are included based on Co, Cr, Fe, and Ni and incorporating at least one of Al, Mo and Ti therein, wherein Co and Ni each has an atomic percentage between 20% and 35%, Cr and Fe each has an atomic percentage between 12.5% and 20%, and the sum of the atomic percentage of Co, Ni, Cr, Fe is no less than 65%, while the sum of the atomic percentage of Al, Mo and Ti lies between 5% and 25%. Further, the property of the alloys can be improved by incorporating sub elements such as Ag, B, C, Cu, Mn, Nb, Ta, Si, V, W, Y, Zr with the sum of the atomic percentage thereof no more than 10%.

Description

200806801 IX. Description of the invention: [Technical field to which the invention pertains] This is a high-temperature alloy with a low-rotation content, especially, V - · [Prior Art] Conventional alloy systems are iron, copper, Shao, Zhen, Chin, wrong, wrong, Ming class 丄 For a long time, the development of the conventional alloy system, mainly a 兀 兀 兀 ( ( ( ( (atomic percentage of at least 50%) and with it to improve the properties of the alloy. For example, ferroalloys:, =ί, but the alloy design and the choice of alloys are still not based on a 70-based concept. Two studies on bulk amorphous alloy materials that have arisen in the past ten years or so have been calculated as follows: (1) the difference in the radius of the two-phase heteroatoms is more than 12%; (7) the at least three elements ϋϋ = a large mixture. However, according to the reading published by the age class, it can be found that the S:: ΐ is the main element, at least 4 〇% atomic ratio, such as iron-based, titanium-based, magnesium-based, hammer-based amorphous alloy. The development of the δ-gold system is limited to one or two main elements, which inevitably limits the freedom and space of alloy development. Therefore, the father of the 199-tone five-year-old new concept of the alloy "multiple ageing gold", that is, at least the main element of the alloy to configure the alloy, so that the degree of freedom of the alloy composition is greatly increased, so add new, crystal structure, , the development of structure and new performance. Specifically, in thermal dropout, the high entropy under the multi-ruthenium alloy contributes to the reduction of the system's free energy, and the solid-phase phase of the household arrangement, rather than the ordered arrangement of the second material, thus reducing the brittleness. The phenomenon occurs. Liugan crystal has 12 sliding systems, usually with better deformability. Because its strength is less sensitive to temperature changes, its strength is less than 0 200806801 at high temperatures. This is also nickel-based, cobalt-based and Iron-based superalloys must be based on FCC crystallization. Because of the high raw material cost of the guji, followed by nickel-based, iron-based is the cheapest, the present invention provides a novel alloy system that can reduce the amount of cobalt-nickel used. The invention can be based on the FCC crystal structure, and thus increase the wider industrial utilization. SUMMARY OF THE INVENTION The object of the present invention is to improve the low-cobalt nickel content and the FCC crystal-based high temperature resistant alloy by using the design of the multi-component alloy. The alloy is based on CoCrFeNi quaternary alloy and at least one of Al, Mo and Ti is added as the main element to form a multi-component 'gold'. The atomic percentage of C〇 and parent elements is between 20% and 35%. • Cr and the atomic percentage of each element are between 12.5% and 20%, and the sum of Co, &, ?6 and see atomic percentages exceeds 65%, and 8.1, ^^〇 or The sum of the atomic percentages of 11 is between 5% and 25%. In addition, you can add Ag, B, C, :〇1,_1, Yang), 乜, 义, ¥, hip, ¥, & The characteristics of the alloy, but the sum of the atomic percentages of the added minor elements shall not exceed 10%. The alloy system may be represented by the composition of ((:0,〇^,>^]^>^, where]^[兀素可And at least one selected from the group consisting of Al, Mo, and Ti, wherein the element is a secondary element such as at least one selected from the group consisting of Ag, B, C, Cu, Mn, Nb, Ta, Si, V, w, Y, and Zr. Calculated as atomic percentage, x^65%, 5Sy^25%, and 〇<zgl〇%, where φ Co&Nl has an atomic percentage of each element between 20% and 35%, and Cr and • Fe per The atomic percentage of each element is between 12.5% and 20%. The alloy can be melt-cast and cast by conventional hot-casting methods such as hot wire heating, induction heating, vacuum arc volumetric refining, etc. Rapid solidification method, mechanical alloy And alloying by powder metallurgy or the like, and can be used for metal processing such as subsequent forging processing, homogenization heat treatment and rolling processing. According to an embodiment of the present invention, n kinds of high are prepared by designing the above multi-alloy alloy The entropy alloy test piece, based on C〇15CrFeNil·5, is added with an appropriate amount of A, Μ, Ή, and has good alloy properties after vacuum arc smelting. The addition of Al, Mo and Ti to this alloy system c 〇15CrFeNiL5 has different degrees of strong 200806801, obviously Ti has the best effect, followed by Mo, followed by A1. According to an embodiment of the present invention, after the test piece of CouCrFeNiLsTioj is subjected to processing, homogenization heat treatment and rolling processing, the microstructure and hardness of the test piece in each state are observed. The results show that the alloy has excellent temperature resistance and work hardening ability. ^ According to one of the implementations of this Fen Ming, the other 11 kinds of high-entropy alloy test pieces were prepared by using the above-mentioned multi-alloy design, and the appropriate amount was added with Co2CrFeNi2 as the base alloy.

Al, Mo, Ti have good alloy properties after vacuum arc smelting. The addition of Al, Mo and Ti has different degrees of strengthening effect on the alloy system c〇2CrFeNi2. Obviously Ti has the best effect, followed by Mo, followed by A1. i According to an embodiment of the present invention, the test piece of c〇2CrFeNi2Ti〇5 was subjected to forging k processing, homogenization heat treatment and rolling processing, and the hardness and structural changes of the test piece in each state were observed. The results show that the alloy has excellent temperature resistance and work hardening ability. According to the consistent application of the present invention, another 18 kinds of high-entropy alloy test pieces are prepared by using the above-mentioned multi-alloy design, wherein an appropriate amount of secondary elements such as 八, ^, (::〇:1, ^Nb'Ta, Si are added. At least one of V, W, Y, and Zr is used to prepare a multi-element alloy. The total amount of the sub-mass is not more than 1% by atom, and the hardness value of the alloy test piece varies depending on the element of the addition force ^. The hardness, ductility and processability can be adjusted according to different addition amounts to suit the unconstrained degree, especially in the application of high temperature structure. One embodiment and another embodiment of the alloy can also be cast after real arc smelting The hardening treatment is carried out by a high-temperature aging method. The above-mentioned multi-equivalent high-entropy alloy is a machinable and analyzable alloy material, and is an alloy having good work hardening, high temperature age hardening, and (four) temperature characteristics. The embodiments of the present invention are intended to facilitate the disclosure of the present invention. Where appropriate, the same reference numerals are used to represent the same. The embodiments described herein are intended to be illustrative only and not limiting. Π This invention is not to be construed as being limited by the embodiments of the present invention, and any equivalents thereof. Further, in the embodiment of the present invention, the hardness of the alloy test piece, test f CMATSUZAWASEK·" The measuring surface is sequentially _, (4) 0, #240, _0, #_, #_上上上平平平平平平平平平平平平平平平平平平平平平平平The hardness value of the position is averaged as the average of the five intermediate averages. The observation structure is made by using a water-cooled grinder to cut the test piece so that it affects the microstructure of the cut surface. #180 #240, _〇, #_, #_, #1细, (4) (10), #狮之沈TFm <;4川^> / For, etching, etching with optical microscope (0M) and F The electron microscopy (SEM) was used to observe the microstructure, and the composition analysis was carried out by EDS (n political cloth analyzer). γ丄f L Bu, the phase of the crystal structure was taken from the ixi5xi5mm test piece. The postal code is deleted - FM2X ray diffractometer, you command the helmet to shoot 1 source for x-ray intensity measurement. The operating voltage is 3〇kv, f (10) is 2〇mA, The scanning range is from 2〇 to 100 degrees, and the scanning speed is 4 degrees/min. Example 1: Table 1 is the alloy composition selected in this example. The test piece number is from the dish to ^ C〇L5CrFeNlL5 as the base alloy (the dimension of the alloy) The hardness is HV113, which is m: 曰5 structure}, and an appropriate amount of A1, Ti, and Mo is added to prepare a multi-component alloy. The purity of the raw materials of the households is above 99%. Table 2 _ is the alloy of the invention The individual basic characteristics of the pigment, including atomic weight, size, melting point, hysteresis, post-degree, crystal structure and crystal structure conversion temperature. 200806801 The composition of the alloy dad j tiger: (the right seven blocks are atomic percentage) In terms of atomic ratio, Co Cr Fe - 曰, Ni AI Ti Mo HK1 CoL5CrFeNiL5 Al〇5 27.3 18.2 18.2 27.3 9.0 HE2 CoL5CrFeNiL5Ti〇.5 27.3 18.2 18.2 27.3 0 9.0 0 HE3 CoL5CrFe NiL5Mo〇.5 273 18.2 18.2 273 0 . 0 9.0 HE4 CoL5CrFeNiL5Al 25.0 16.7 16.7 25.0 16.6 0 0 HE5 CoL5CrFeNiL5Ti 25.0 16.7 16.7 25.0 0 16.6 0 HE6 C〇i.5CrFeNiL5Mo 25.0 16.7 16.7 25.0 0 0 16.6 HE7 Co1.5CrFeNiL5Al〇.5Ti〇.5 25.0 16.7 16.7 25.0 83 8.3 0HE8 Co15CrFeNiL5Al0.5Mo0.5 25.0 16.7 16.7 25.0 8.3 0 8.3 HE9 Co15CrFeNiL5Ti 0.5M00.5 25.0 16.7 16.7 25.0 0 8.3 8.3 HE10 COi.5CrFeNii.5Alo.5Ti 〇.5Μ〇0·5 23.1 15.4 15.4 23.1 7.7 7.7 7.6 HE11 CoL5CrFeNiL5Al 〇.25 Ti 0.5M00.25 25.0 16.7 16.7 25.0 4.15 8.3 4.15 9 200806801 Table 2: Basic characteristics of alloying elements Element A1 Ti Co Cr Fe Mo Ni Atomic weight (g/mole) 26.98 47.867 58.93 52.00 55.85 95.94 58.69 Atomic radius (A 1·18 L76 1.52 1.66 1.56 1.9 1.49 Melting point fc) 660 1668 1495 1907 1538 2623 1455 Boiling point (°C) 2519 3287 2927 2671 2861 4639 2913 Density (g/cm3) 2.70 4.053 8.9 7.14 7.87 10.28 8.91 Crystal structure (low temperature) FCC HCP HCP BCC BCC BCC FCC Crystal Structure (High Temperature) FCC BCC FCC FCC FCC, BCC BCC FCC Crystal Structure Conversion Temperature (°C) 417 1840 910 1390 FIG. 1 is a process for preparing and processing an alloy according to an embodiment of the present invention. As shown in Fig. 1, in the present embodiment, a vacuum arc melting furnace can be used to melt the alloy, and it can be used for subsequent forging processing, homogenization heat treatment, rolling processing, and hardening treatment. Then hardness measurement, X-ray diffraction analysis, microstructure observation and composition analysis were performed. In the smelting, the pure metal particles with a total weight of about 50 g are first placed on a water-cooled copper mold, the upper cover of the furnace is covered, the vacuum is evacuated to 0 01 atm, and then pure argon gas is introduced to 〇 2 atm. In order to avoid a large amount of oxidation of the alloy, the evacuation process as described above is repeated three times, and the smelting process is performed, wherein the smelting current is 5 amps. When the metal block has been dissolved = uniform and after it has been cooled, the metal block is turned over and then smelted, so that it is repeated several times until all the alloying elements have been dissolved and mixed (10), and the * part solidifies to form a casting or ingot. . ..., silly, 1 10 200806801 The eleven alloys prepared according to Table 1, both of which have good alloy properties. I and the two bodies and the hardness and hardness are shown in Table 3.

The addition of Ti shows that the alloy system CGi5Cl:FeN^ is visible as 'A1' Mo, and the same degree of coffee, the effect of Ti is not A1. In addition, the addition of the three elements is increased: hard ^ ^ 〇 ' = skillfully will form a BCC (body core cube) phase, but to? Sheet metal can adjust the hardness, the s should be under the test, especially the high temperature. J5$ No. HE1 HE2 Alloy Casting! Double structure and hardness (foot) or minute (in atomic ratio) gouCrFeNi!^^ ^i.5CrFeNiL5Ti〇.5

C〇uCrFeNiL5 Mo〇, 5 £〇i: sCrFeNi1.5Al £2uCrFeNiL5Ti

Crystal vine structure FCC FCC FCC FCC+BCC FCC+BCC hardness 136 378 193 277 581 HE6 C〇i.5CrFeNiL5Mo

FCC+BCC 394 HE7 C〇i^FeNiL5Al〇.5Til 0.5

FCC+BCC 385 HE8 ££uCrFeNiL5Al〇.5Mo 0.5

FCC+BCC 200 HE9 £2L5CrFeNii.5Ti 〇.5M〇, 0.5

FCC+BCC 417 HE10 c〇L5CrFeNiL5Al〇.5 Ti cross. Wonder 0.5

FCC+BCC 561 HE11

Coi.sCrFeNii.sAlo.^ Ti 〇*5M〇0.25

FCC+BCC 383 Example 2: As shown in Figure 1, the process of preparation and processing of the alloy is carried out. The test piece of the HE2 alloy CouCrFeNUi^ in the first embodiment is placed in a high temperature furnace 1000 C for 15 minutes, and then taken out and pneumatically used. Type hammer forging machine (Model: OT-1521280) for hot forging, 11 200806801 Load 250kg, processing capacity is 40%. Next, the forged test piece was placed in a heat treatment furnace, homogenized at 1 UKTC for 24 hours, and then subjected to furnace cooling and water quenching, respectively. The hardness of each stage was as shown in Table 4, and the hardness after forging. Increase by about 30%. The homogenization furnace has a lower cooling hardness, but the water quenching is slightly higher. It can be found that the alloy does not exhibit a temperature softening phenomenon of 1100 C, indicating that the alloy has superior temperature resistance. The sorrowful crystal structure of each shape is analyzed by X-ray diffraction, and all still have a single Fee phase. Table 4: CouCrFeNii 5Ti〇.5 alloy by casting degree (HV) South temperature forging and homogenization hard

First, 'the alloy test piece cold-treated in the homogenization furnace is used to control the hardness of the alloy test piece...the type=DBR250 is rolled. The processing volume is 0%, 5 respectively. %, 15%, 3〇%, 8〇%. The results obtained are shown in Table 5. The alloy test piece has obvious work hardening with the increase of the processing amount of the rolling processing. The hardness after processing is greatly increased, and the hardness is about increased after processing 3〇0/〇. 1.78 times before. Thus, the alloy exhibits excellent work hardening characteristics. X-ray diffraction analysis shows that the c〇i5CrFeNii5Ti()5 alloy increases with the processing amount, and the diffraction peak of the FCC gradually decreases. This is because the crystal lattice will produce more deformation and distortion after the alloy is processed. The X-ray produces a large amount of diffusing effect. Processing volume 0% γΐ·5“〇·5, mouth 5%/Meng: via a mouth JZ 15% 丄 浓 / 3⁄4 30% 80% hardness 313 467 452 558 545 Example 3 Table 6 is the embodiment The alloy composition selected, the test piece number is HE12 to HE22 'Cc^CrFeNi2 based alloy (the Vickers hardness of the alloy is hv108, the FCC crystal structure of 12 200806801), and the appropriate amount of A1, Ti, Mo is added to prepare the diversified The raw material purity of the elements used in the alloy is above 99%. & f 6··ΗΕ12-ΗΕ22 Alloy 24^ Right Qi Qiao

The addition of Mo and Ti to this alloy is Γ n /, body and έ, as can be seen from Table 7, A1, especially for applications under high temperature structures. Workers are looking for suitable for different strengths. 13 200806801 Table |7: Crystal Structure and Hardness (Ηγ) No.----- Composition (in atomic scale) 33⁄4 bottle box Hardness 1 1 丨124 HE12 Co2CrFeNi2 Al〇5 ^^' HE13 Co2CrFeNi2 Ti: ^ ----- FCC 340 HE14 Co2CrFeNi2 Mo〇5 FCC 170 HE15 Cc^CrFeisi: Ai FCC+BCC 230 HE16 Co2CrFeNi2 Ti FCC+BCC 456 HE17 Co2CrFeNi2 Mo FCC+BCC 236 HE18 Co2CrFeNi2Al05Ti0s FCC+BCC 356 HE19 C〇2CrFeNi2Al0.5Mo0, FCC+BCC 180 HE20 Co2CrFeNi2Ti 5.5Mo〇s FCC+BCC 316 HE21 Co2CrFeNi2Al〇.5 Ti 0,5Mon, FCC+BCC 376 HE22 Co2CrFeNi2Al 〇.25 Ti 0.5M00.25 FCC+BCC 349 Example 4: The test piece of HE13 alloy C〇2CrFeNi2Ti〇·5 in Example 3 was placed in a high temperature 1000 C for 15 minutes, and then taken out using a pneumatic hammer. Forging machine (model: Pie 10 OT-1521280) for hot forging, load 250kg, processing capacity is 40%. Next, the forged ▲ test piece was placed in a heat treatment furnace, and after homogenization treatment at ll 〇〇 ° C for 24 hours, the furnace cooling and water quenching were respectively carried out, and the hardness of each stage was as shown in Table 8. Show, ^ The hardness after forging is increased by about 28%. The homogenization furnace has a cold hardness increase, but the water quenching is about constant, and it can be found that the alloy does not exhibit a 1100 C south temperature softening phenomenon, indicating that the alloy has superior temperature resistance characteristics. The crystal structures of each state are still analyzed by X-ray diffraction, and all still have a single FCC phase. 14 200806801

He<)2(>FeNi2TiG.5 alloy cast (HV) high temperature satin and homogenized hardness

Rain temperature forging 421 Six quality furnace cooling 403 328

Co2CrF^i〇Ti05

The use of double S pressure, the amount of processing Α Π () / two ~ 疋 ~ take the soap to grasp the burial from the observation of the hardness change shown, the wide 15 ° ί, 3. %, 7. %. The results obtained are as shown in Table 9. After the second hardness, the hardness is greatly increased, and the force is strong. It is shown by \光^7^^ that the alloy has excellent work hardening and special irr Λ 6 rounds of lying 1 to the ship 21 ^ alloy age processing volume increased, larger ίίίί gradually decreased 'this is because the alloy is processed, The crystal lattice will produce more distortion and distortion, which in turn will cause a large amount of diffusing effect on the X-ray. Processing amount 0% 5% 15% 30% 70% " Hardness 328 335 416 515 566 15 1 Example 丄 - Table 忉 is the alloy composition selected in this example, the test piece number is ΗΕ23 to ΗΕ40. This is an alloy based on ΗΕ1-ΗΕ9 (as shown in Table 1) and ΗΕ12-20 (as shown in Table-6) as the base alloy, adding appropriate amounts of secondary elements such as Ag, Β, C, Cu, Μη, Nb, At least one of Ta, Si, V, W, yttrium, Zr, etc., to prepare a multi-element alloy. The raw materials used in the configuration have a purity of more than 99%. 200806801 Table 10·············· 17.5 17.5 263 8.9 0 0 Ag: 3.5% HE24 Co1.5CrFeNiL5Ti〇.5B〇.1C〇.1 26.3 17.5 17.5 263 0 8.9 0 B 丄75%, C:L75% HE25 Co15CifeNi1.5Mo0.5Si〇.2 26.3 17.5 17.5 263 0 0 8.9 Si: 3.5% HE26 CoL5CrFeNiL5Al Cu〇.2Mn〇3 23.1 15.4 15.4 23.1 15.4 0 0 Cu: 3.0%, Mn: 4.6% HE27 Co13CrFeNi1.5Tim〇.1V〇2 23.8 15.9 15.9 23.8 0 15.8 0 Nb :1.6%9 V:3.2% HE28 Co15CrFe Nii^MoNbo j V 0.2W03 22.7 15.1 15.1 22.7 0 0 153 Nb: 1.5%, V: 3%, W: 4.6% HE29 CoL5CrFeNiL5Al〇.5Ti〇.5 Ta〇.2Zr0&gt ;1 23.8 15.9 15.9 23.8 7.9 7.9 0 Ta: 32%, Zr: 1.6% HE30 C〇i.5CrFeNiL5Al〇.5Mo〇.5 V0.2Y0.1 23.8 15.9 15.9 23.8 7.9 0 7.9 V: 3.2%, Y: 1.6 % HE31 C〇i.5CrFeNi15Ti 0.5M〇05 Ta〇.iY〇.i 24.2 16.1 16.1 24.2 0 8.1 8.1 Ik 1.6%, Y:L6% HE32 Cc^CrFeNi]Alas Ag〇.2 29.8 14.9 14.9 29.8 7.4 0 0 Ag: 3% HE33 Co2CrFeN i2Tia5BaiCai 29.8 14.9 14.9 29.8 0 7.4 0 Β:1·5%, C:1.5% HE34 Co2CrFeNi2 Mo〇.5 Si〇.2 29.8 14.9 14.9 29.8 0 0 7.4 Si:3% HE35 Co2CrFeNi2 Al Cu〇2Mn〇3 26.7 133 13.3 26.7 13.3 0 0 Cu: 2.7% 5 Mn: 4.0% HE36 Co2CrFeNi2TiNbaiVa2 27.4 13.7 13.7 27.4 0 13.7 0 Nb: 1.4%, V: 2.7% 16 200806801 HE37 Cc^CrFelSfyVloNbaiVoWM 263 13.2 13.2 263 0 13.2 Nb: L3%, V : 2.6%, w-3 g〇/a HK38 CG2CrFeNi2Al〇.5Ti〇.5 Ta〇.2Zr0>i 27.4 13.7 13.7 27.4 6.8 6.8 0 Ta:2.8%, 7r-l 4% HE39 Co2CrFeNi2Al〇.5Mo05 V0.2Y0 .1 27.4 13.7 13.7 27.4 6·8 0 6.8 £Λ · 1 .Τ' /〇V: 2.8%, HE40 Co2CrFeNi2Ti 〇.5M〇〇5 Ta〇.iY〇, 27.8 0 6.9 Y: 1.4% Ta: L4% ? Y: 1.4% as shown in Table & (d)) crystal structure and hardness · a ^ b ; ^ u ;

Mn, Nb, Ta, Si, v, w, Y, and added elements vary. In addition, Table 3, Table 7, and Table: J are removed from the addition of Ag and Cu, and the addition of other minor elements is ♦ basic ^ 2 hard ff rise. The addition of the interstitial part will increase the BCC phase, and the main 曰曰fi?, so the hardness and ductility can be adjusted by different addition amounts to suit the application of different strengths, especially under high temperature structure. The should be 17 200806801 HE23-HE40 alloy tungsten pieces of crystal knots invited to the Tang (HV) number component (in atomic ratio), 丄丄 \ crystal structure hardness HE23 〇〇! 5CrFeNiL5 Al〇.5Ag〇2 FCC 125 HE24 C 〇i.5CrFeNii.5Ti〇5 B〇iC〇1 FCC + collar carbide phase 424 HE25 CoL5CrFeNiL5 Mo〇5Si〇2 FCC + BCC 231 Human A 0〇! 5CrFeNii 5A1 Cu〇2ivln〇^ FCC+BCC 257 HE27 CoL5CrFeNiL5TiNb01V02 FCC+BCC 715 HE28 CoL5CrFe NiL5MoNb〇! V〇9W〇^ FCC+BCC 732 HE29 CoL5CrFeNiL5 Al〇>5Ti0 5 Ta〇.2Zr〇! FCC + BCC 590 HE30 CoL5CrFeNiL5Al〇.5Mo〇.5 V〇.2Y〇, FCC+BCC 271 HE31 CoL5CrFeNiL5Ti 〇.5M〇〇s Ta〇! Y〇, FCC + BCC 626 HE32 Co2CrFeNi2Al〇.5 Ag〇2 FCC 110 HE33 Cc^CrFeNi: Ti〇5 B〇jCoji FCC + shed carbide phase 356 HE34 Co2CrFeNi2 Mo〇, 5 Si〇2 FCC 177 HE35 Co2CrFeNi2 A1 Cu〇 .2Mn〇3 FCC + BCC 201 HE36 Co2CrFeNi2 FCC + BCC 529 ΠΕ37 Co2CrFeNi2 Mo Nb〇H FCC+BCC 580 HE38 C02CrFeNi2Alo.5Tio.5Tao.2Zro” FCC+BCC 556 HE39 Co2CrFeNi2Al0.5Mo0.5 V〇.2Y(u FCC + BCC 229 HE40 Co2CrFeNi2Ti0,5Mo0.5 Tao.iYo" FCC+BCC 503 Further, according to another embodiment of the present invention, for example, a Co^CrFeNiuTio.5 alloy test piece is cast by vacuum arc melting, at a high temperature Efficient hardening treatment. The cast test piece was placed in a heat treatment furnace at 4 Torr (TC, 600 ° C, 800 ° C for 1 hr, 2 hr, 5 hr, 10 hr. The results are shown in Table 12, under conditions of 800 T, observable To the rare high-temperature age hardening phenomenon, the hardness of the alloy can be increased from 378HV to 513HV after 5hr aging. After 10hr aging, the hardness of the alloy becomes 18 200806801. Before the aging, 33 times\hours, 'w\inter-degree \^ Ohr Ihr 2hr 5hr lOhr 400 °C 378±10·0 388±3·8 408+9.1 362±4.2 382+5.9 ^ 378+10.0 400+2.3 387+6.5 384+12.2 387±10.5 800 °C 378110. G 470±7·7 485±6.1 513±4.1 503±7.0 In summary, it can be understood that the alloy system of the present invention can be represented by ((^, 0, 1 <^]\471^, wherein] ^[The element may be selected from at least one of VIII, ^^0 and Ti, and the N element is a secondary element such as Ag, B, c, cu, Mn, :N[b, Ta, Si, V, W, Y, At least one of Zr and the like, calculated as atomic percentage, x^65%, 5$yS25%, and OCz^lO%, wherein each atomic percentage of C〇&Ni is between 20% and 35%, and The atomic percentage of each element of Cr&Fe is between 1 2.5% to 20%. The phase of the alloy system in the as-cast state is dominated by the phase of the Fcc crystal structure. In crystallography, the sFCC phase has 12 sliding systems, which are easy to slide and deform, so it is usually quite ductile. In addition, the FCC phase is strong, the temperature is more peachy, and it is stronger at high temperatures. Therefore, the alloy can provide different hardness. Whether it is applied at room temperature or high temperature structural application, it can be the same strength. And the need for ductility, the person who obtains the appropriate characteristics by the adjustment of the composition - In addition, the alloy system of the present invention contains & and (:: 〇, see each at least the original: ==, _ _ and anti-oxidation Too 妒^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^ Those skilled in the art should understand that in the embodiment of the present invention, as shown in FIG. 19, 200806801, the force of 働=====: i is the age of the if. j or processing 'without all the details of this operation, the implementation of this issue, only to explain the exemplary implementation of the present invention Embodiment, whenever skilled in the 'art-known private The above description is merely illustrative and not limiting, without departing from the i-shaped rail of the present invention preferably change, the changes may be revised based on the various lines Que green solid. Accordingly, all such modifications are considered to be included within the scope of the invention. BRIEF DESCRIPTION OF THE DRAWINGS Fig. 1 is a flow chart showing the preparation and processing of an alloy according to an embodiment of the present invention. [Main component symbol description] No flaw 20

Claims (1)

200806801 X. Patent application scope: 1. - A low-temperature resistant alloy with a composition of (Co, CrJFe, M) x MyNz ' where: (〇〇, α: ^, Μ) X indicates that XS is 65%, wherein the atomic percentage of each element of p and Νι is between 2% and 35%, and the other atomic percentage of each element is between 12.5% and 2〇. Between %; the atomic percentage of Fe Μ element is represented by γ, % γ ^ 25%, and the & is selected from at least one of AL·Mo and Ti; the atomic percentage of the elemental N element is represented by z, 〇 <ζ$1〇%, and the N » is selected from Ag, B, c, Cu, Μη, her, Ta, Si, v, w, γ, Zr to small, "糸_ 〇2. The high-temperature alloy of low cobalt and nickel content in the first item of the patent scope, wherein the human gold is formed by dissolving tungsten by vacuum electric soaking. 3. A high-temperature alloy of low cobalt nickel content as claimed in claim 1 or 2, which is mainly composed of FCC crystal phase. ^ Τ 4· A high-temperature alloy of low cobalt nickel content as claimed in claim 1 or 2, wherein the alloy is processed by forging. 5. Repair the high-temperature alloy of low-nickel nickel content according to the first or second patent application scope, and the gold and gold are heat treated by homogenization. 6. If the high-temperature alloy of low-loss nickel content of the 1 or 2 item of the patent scope is applied, the alloy is processed by rolling. 7. A high-temperature alloy of low inscription content, such as the claim 1 or 2, in which the alloy is subjected to hardening treatment. XI. Schema: 21