TW202206617A - Methods for increasing stress fracture life of nickel-based superalloys The present invention provides a method for improving the stress rupture life of a nickel-based superalloy - Google Patents
Methods for increasing stress fracture life of nickel-based superalloys The present invention provides a method for improving the stress rupture life of a nickel-based superalloy Download PDFInfo
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本發明係關於一種提升鎳基超合金應力破斷壽命之方法，特別是關於一種透過鉭元素添加之提升鎳基超合金應力破斷壽命之方法。 The present invention relates to a method for increasing the stress rupture life of a nickel-based superalloy, in particular to a method for increasing the stress rupture life of a nickel-based superalloy by adding tantalum element.
鎳基合金多應用於航空產業中，發動機的關鍵零組件上，正因如此，材料的耐用度顯得格外重要。如以碳含量0.01-0.05wt%、磷含量0.004-0.020wt%、鉻含量17.00-21.00wt%、鉬含量2.50-3.10wt%、鈮含量5.20-5.80wt%、鈦含量0.50-1.00wt%、鋁含量1.20-1.70wt%、鈷含量8.00-10.00、鎢含量0.80-1.40、硼含量0.003-0.008wt%、鐵含量8.00-10.00wt%之鎳基超合金而言，其AMS 5441規範載明，於704℃/621MPa之應力破斷壽命不得低於39小時。 Nickel-based alloys are mostly used in the aviation industry and key components of engines. Because of this, the durability of the material is particularly important. For example, the carbon content is 0.01-0.05wt%, the phosphorus content is 0.004-0.020wt%, the chromium content is 17.00-21.00wt%, the molybdenum content is 2.50-3.10wt%, the niobium content is 5.20-5.80wt%, and the titanium content is 0.50-1.00wt%. For nickel-based superalloys with aluminum content of 1.20-1.70wt%, cobalt content of 8.00-10.00, tungsten content of 0.80-1.40, boron content of 0.003-0.008wt%, and iron content of 8.00-10.00wt%, the AMS 5441 specification states, The stress rupture life at 704℃/621MPa shall not be less than 39 hours.
如專利CN101142338，鎳基合金和直接時效熱處理的方法，發明直接時效718Plus鎳基合金的方法。其實施例1的鍛造718Plus合金於704℃/552MPa之應力破斷試驗，採用直接時效熱處理之最高壽命為515小時，採用固溶加時效熱處理之最高壽命為360小時。 For example, the patent CN101142338, the method of nickel-based alloy and direct aging heat treatment, invented the method of direct aging 718Plus nickel-based alloy. In the stress rupture test of the forged 718Plus alloy of Example 1 at 704°C/552MPa, the maximum life of the direct aging heat treatment was 515 hours, and the maximum life of the solution and aging heat treatment was 360 hours.
上述碳含量0.01-0.05wt%、磷含量0.004-0.020 wt%、鉻含量17.00-21.00wt%、鉬含量2.50-3.10wt%、鈮含量5.20-5.80wt%、鈦含量0.50-1.00wt%、鋁含量1.20-1.70wt%、鈷含量8.00-10.00、鎢含量0.80-1.40、硼含量0.003-0.008wt%、鐵含量8.00-10.00wt%之鎳基超合金其應用溫度約為704℃，原因係為合金中之gamma double prime(γ")於該溫度下會轉變為delta phase(δ)，使得強度下降，耐用度大幅衰退。 The above carbon content 0.01-0.05wt%, phosphorus content 0.004-0.020wt%, chromium content 17.00-21.00wt%, molybdenum content 2.50-3.10wt%, niobium content 5.20-5.80wt%, titanium content 0.50-1.00wt%, aluminum content The application temperature of nickel-based superalloys with a content of 1.20-1.70wt%, a cobalt content of 8.00-10.00, a tungsten content of 0.80-1.40, a boron content of 0.003-0.008wt%, and an iron content of 8.00-10.00wt% is about 704 °C. The reason is that The gamma double prime (γ " ) in the alloy will be transformed into delta phase (δ) at this temperature, resulting in a decrease in strength and a significant decline in durability.
綜上所述，目前材料科學家仍致力於改善合金強度、耐溫性、抗氧化性、抗潛變性...等，其中應力破斷壽命可謂綜合上述各項特性之表現，本案之申請人經苦心研究發展出了一種提升鎳基超合金應力破斷壽命之方法，以延長合金之應力破斷壽命。 To sum up, at present, material scientists are still working on improving the strength, temperature resistance, oxidation resistance, latent modification resistance of alloys, etc. Among them, the stress rupture life can be described as the performance of the above-mentioned characteristics. Painfully researched and developed a method to increase the stress rupture life of nickel-based superalloys, so as to prolong the stress rupture life of alloys.
鑒於上述悉知技術之缺點，本發明之主要目的在於提供一種提升鎳基超合金應力破斷壽命之方法，利用金屬鉭(Tantalum)元素屬於高熔點耐火元素，高溫下具有穩定結構、高延展性、抗氧化等特性，因此本發明構想為透過鉭元素添加至上述碳含量0.01-0.05wt%、磷含量0.004-0.020wt%、鉻含量17.00-21.00wt%、鉬含量2.50-3.10wt%、鈮含量5.20-5.80wt%、鈦含量0.50-1.00wt%、鋁含量1.20-1.70wt%、鈷含量8.00-10.00、鎢含量0.80-1.40、硼含量0.003-0.008 wt%、鐵含量8.00-10.00wt%之鎳基超合金中，以延長合金之應力破斷壽命。 In view of the shortcomings of the above-mentioned known technologies, the main purpose of the present invention is to provide a method for improving the stress rupture life of nickel-based superalloys, using metal tantalum (Tantalum) element, which is a high melting point refractory element, and has stable structure and high ductility at high temperature. , anti-oxidation and other properties, so the invention is conceived to add tantalum to the above-mentioned carbon content of 0.01-0.05wt%, phosphorus content of 0.004-0.020wt%, chromium content of 17.00-21.00wt%, molybdenum content of 2.50-3.10wt%, niobium content content 5.20-5.80wt%, titanium content 0.50-1.00wt%, aluminum content 1.20-1.70wt%, cobalt content 8.00-10.00, tungsten content 0.80-1.40, boron content 0.003-0.008 wt%, the iron content of 8.00-10.00wt% of nickel-based superalloys, in order to prolong the stress fracture life of the alloy.
為了達到上述目的，根據本發明所提出之一方案，提供一種提升鎳基超合金應力破斷壽命之方法，步驟包括：(A)提供一鎳基超合金，該鎳基超合金之成分包括：碳含量0.01-0.05wt%、磷含量0.004-0.020wt%、鉻含量17.00-21.00wt%、鉬含量2.50-3.10wt%、鈮含量4.80-5.80wt%、鈦含量0.50-1.00wt%、鋁含量1.20-1.70wt%、鈷含量8.00-10.00wt%、鎢含量0.80-1.57wt%、硼含量0.003-0.008wt%、鐵含量8.00-10.02wt%、鉭含量3.63-12.73wt%，其餘則由鎳及無法避免之雜質所構成；(B)將該鎳基超合金以真空感應爐進行一熔煉處理，該鎳基超合金經熔煉後進行一鑄造處理；以及(C)該鎳基超合金經鑄造後係經一熱均壓及一真空熱處理。 In order to achieve the above-mentioned purpose, according to a scheme proposed by the present invention, a method for improving the stress rupture life of nickel-based superalloy is provided, and the steps include: (A) provide a nickel-based superalloy, and the composition of the nickel-based superalloy includes: Carbon content 0.01-0.05wt%, phosphorus content 0.004-0.020wt%, chromium content 17.00-21.00wt%, molybdenum content 2.50-3.10wt%, niobium content 4.80-5.80wt%, titanium content 0.50-1.00wt%, aluminum content 1.20-1.70wt%, cobalt content 8.00-10.00wt%, tungsten content 0.80-1.57wt%, boron content 0.003-0.008wt%, iron content 8.00-10.02wt%, tantalum content 3.63-12.73wt%, the rest are made of nickel and unavoidable impurities; (B) the nickel-based superalloy is subjected to a smelting treatment in a vacuum induction furnace, and the nickel-based superalloy is smelted and then subjected to a casting treatment; and (C) the nickel-based superalloy is cast Afterwards, it is subjected to a hot equalization pressure and a vacuum heat treatment.
較佳地，鑄造處理之澆鑄溫度可為1350-1450℃、模溫可為1050-1150℃，以及真空度須達3.0×10-2Torr。 Preferably, the casting temperature of the casting process can be 1350-1450°C, the mold temperature can be 1050-1150°C, and the vacuum degree must reach 3.0×10 -2 Torr.
較佳地，熱均壓製程參數可為溫度1100-1200℃、施壓1000-1100 bar持續2-4小時。 Preferably, the parameters of the hot equalization pressing process can be a temperature of 1100-1200° C. and a pressure of 1000-1100 bar for 2-4 hours.
較佳地，真空熱處理係可分為一固溶熱處理及一時效熱處理。 Preferably, the vacuum heat treatment system can be divided into a solution heat treatment and an aging heat treatment.
較佳地，固溶熱處理係可以954-982℃的溫度範圍進行熱處理1小時後氣體冷卻至室溫。 Preferably, the solution heat treatment system can perform heat treatment in the temperature range of 954-982° C. for 1 hour and then gas cool to room temperature.
較佳地，時效熱處理係可以788±8℃的溫度範圍 進行熱處理8小時後爐冷至704±8℃持溫8小時再爐冷至室溫。 Preferably, the aging heat treatment system can be in the temperature range of 788±8℃ After heat treatment for 8 hours, furnace-cooled to 704±8°C for 8 hours and then furnace-cooled to room temperature.
較佳地，鉭含量為8.7-12.73wt%時，鎳基超合金經溫度704℃及壓力621MPa之應力破斷試驗所得應力破斷壽命係可大於300小時。 Preferably, when the tantalum content is 8.7-12.73 wt %, the stress rupture life of the nickel-based superalloy through the stress rupture test at a temperature of 704° C. and a pressure of 621 MPa can be greater than 300 hours.
以上之概述與接下來的詳細說明及附圖，皆是為了能進一步說明本發明達到預定目的所採取的方式、手段及功效。而有關本發明的其他目的及優點，將在後續的說明及圖式中加以闡述。 The above summary, the following detailed description and the accompanying drawings are all for the purpose of further illustrating the manner, means and effect adopted by the present invention to achieve the predetermined object. The other objects and advantages of the present invention will be explained in the following descriptions and drawings.
S1、S2、S3:步驟 S1, S2, S3: Steps
T0:無添加鉭之鎳基超合金 T0: Nickel-based superalloy without added tantalum
T4:含4wt%鉭之鎳基超合金 T4: Nickel-based superalloy containing 4wt% tantalum
T8:含8wt%鉭之鎳基超合金 T8: Nickel-based superalloy containing 8wt% tantalum
T12:含12wt%鉭之鎳基超合金 T12: Nickel-based superalloy containing 12wt% tantalum
第一圖係為本發明之提升鎳基超合金應力破斷壽命之方法流程圖。 The first figure is a flow chart of the method for improving the stress rupture life of nickel-based superalloys according to the present invention.
第二圖係為不同鉭含量之鎳基超合金之應力破斷壽命圖。 The second graph is a stress rupture life graph of nickel-based superalloys with different tantalum contents.
第三圖係為不同鉭含量之鎳基超合金之Larsen Miller Parameter圖。 The third figure is a Larsen Miller Parameter diagram of nickel-based superalloys with different tantalum contents.
第四圖係為不同鉭含量之鎳基超合金之金相圖。 The fourth figure is a metallographic diagram of nickel-based superalloys with different tantalum contents.
以下係藉由特定的具體實例說明本發明之實施方式，熟悉此技藝之人士可由本說明書所揭示之內容輕易地了解本創作之優點及功效。 The following describes the implementation of the present invention with specific examples, and those skilled in the art can easily understand the advantages and effects of the present invention from the contents disclosed in this specification.
本發明在於提供一種提升鎳基超合金應力破斷壽命之方法，利用金屬鉭(Tantalum)元素屬於高熔點耐火元素，高溫下具有穩定結構、高延展性、抗氧化等特性，透過真空感應熔煉技術，將3.63-12.73wt%金屬鉭元素添加至碳含量0.01-0.05wt%、磷含量0.004-0.020wt%、鉻含量17.00-21.00wt%、鉬含量2.50-3.10wt%、鈮含量5.20-5.80wt%、鈦含量0.50-1.00wt%、鋁含量1.20-1.70wt%、鈷含量8.00-10.00、鎢含量0.80-1.40、硼含量0.003-0.008wt%、鐵含量8.00-10.00wt%之鎳基超合金中，並澆鑄成試桿進行熱均壓(Hot Isostatic pressing)與真空熱處理(Vacuum Heat Treatment)，再於704℃下進行552/621MPa應力破斷試驗，以判斷添加鉭元素對鎳基超合金的應力破斷壽命之影響。 The present invention is to provide a method for improving the stress fracture life of nickel-based superalloys, which utilizes the metal tantalum (Tantalum) element, which is a high melting point refractory element, has the characteristics of stable structure, high ductility, anti-oxidation and the like at high temperature, through vacuum induction melting technology , adding 3.63-12.73wt% metal tantalum element to carbon content 0.01-0.05wt%, phosphorus content 0.004-0.020wt%, chromium content 17.00-21.00wt%, molybdenum content 2.50-3.10wt%, niobium content 5.20-5.80wt% %, titanium content 0.50-1.00wt%, aluminum content 1.20-1.70wt%, cobalt content 8.00-10.00, tungsten content 0.80-1.40, boron content 0.003-0.008wt%, iron content 8.00-10.00wt% nickel-based superalloy and cast into a test rod for Hot Isostatic pressing and Vacuum Heat Treatment, and then conduct a 552/621MPa stress rupture test at 704°C to judge the effect of tantalum addition on nickel-based superalloys. Effects of stress rupture life.
更詳言之，請參閱第一圖係為本發明之提升鎳基超合金應力破斷壽命之方法流程圖，步驟包括：步驟S1，提供一鎳基超合金，此鎳基超合金之成分包括：碳含量0.01-0.05wt%、磷含量0.004-0.020wt%、鉻含量17.00-21.00wt%、鉬含量2.50-3.10wt%、鈮含量4.80-5.80wt%、鈦含量0.50-1.00wt%、鋁含量1.20-1.70wt%、鈷含量8.00-10.00wt%、鎢含量0.80-1.57wt%、硼含量0.003-0.008wt%、鐵含量8.00-10.02wt%、鉭含量3.63-12.73wt%，其餘則由鎳及無法避免之雜質所構成。步驟S2，將鎳基超合金以真空感應爐進行熔煉處理，鎳基超合金經熔煉後進行鑄造處理，以及步驟S3，鎳基超合 金經鑄造後係經熱均壓及真空熱處理。藉由添加鉭於鎳基超合金中可(1)提高合金中γ與γ'相最強共價鍵上共價電子對數的統計值，以及原子狀態組數。(2)提高合金中γ'相的組織穩定性。(3)提高了γ'/Ni界面的穩定性。 In more detail, please refer to the first figure, which is a flow chart of the method for improving the stress rupture life of nickel-based superalloy according to the present invention. : Carbon content 0.01-0.05wt%, phosphorus content 0.004-0.020wt%, chromium content 17.00-21.00wt%, molybdenum content 2.50-3.10wt%, niobium content 4.80-5.80wt%, titanium content 0.50-1.00wt%, aluminum content content 1.20-1.70wt%, cobalt content 8.00-10.00wt%, tungsten content 0.80-1.57wt%, boron content 0.003-0.008wt%, iron content 8.00-10.02wt%, tantalum content 3.63-12.73wt%, the rest are determined by Consists of nickel and unavoidable impurities. In step S2, the nickel-based superalloy is smelted in a vacuum induction furnace, and the nickel-based superalloy is smelted and then cast. By adding tantalum to nickel-based superalloys, (1) the statistics of the number of covalent electron pairs on the strongest covalent bonds of γ and γ ' phases in the alloy can be increased, as well as the number of atomic state groups. (2) Improve the microstructure stability of the γ ' phase in the alloy. (3) The stability of the γ ' /Ni interface is improved.
以下，將探討無添加鉭之鎳基超合金T0、4wt%鉭之鎳基超合金T4、8wt%鉭之鎳基超合金T8、12wt%鉭之鎳基超合金T12等不同鉭含量之鎳基超合金之各項實驗結果。 In the following, nickel-based superalloy T0 with no added tantalum, nickel-based superalloy T4 with 4wt% tantalum, nickel-based superalloy T8 with 8wt% tantalum, and nickel-based superalloy T12 with 12wt% tantalum and other nickel-based superalloys with different tantalum contents will be discussed. Various experimental results of superalloys.
本發明以不同鉭含量包括無添加鉭之鎳基超合金T0、含4wt%鉭之鎳基超合金T4、含8wt%鉭之鎳基超合金T8及含12wt%鉭之鎳基超合金T12分別添加至以自行配料之方式熔配碳含量0.01-0.05wt%、磷含量0.004-0.020wt%、鉻含量17.00-21.00wt%、鉬含量2.50-3.10wt%、鈮含量5.20-5.80wt%、鈦含量0.50-1.00wt%、鋁含量1.20-1.70wt%、鈷含量8.00-10.00、鎢含量0.80-1.40、硼含量0.003-0.008wt%、鐵含量8.00-10.00wt%之鎳基超合金，其中鎳的含量隨著鉭增加而減少，以及無法避免之雜質所構成。透過真空感應熔煉將原料熔鑄成四爐試桿，澆鑄參數之澆鑄溫度為1350-1450℃，模溫為1050-1150℃，真空度須達3.0×10-2Torr。所得四爐試桿以Spark-OES進行化學成分分析，分析結果如表1所示。結果顯示，無添加鉭之鎳基超合金T0之爐試桿及含4wt%鉭之鎳基超合金T4之爐試桿中的全元素仍落於規範值之間，符合成分規範，然而含8wt%鉭之鎳基超合金T8之爐試桿之鈮 元素、含12wt%鉭之鎳基超合金T12之爐試桿之鈮、鐵、鎢元素均超出規範，而含4wt%鉭之鎳基超合金T4、含8wt%鉭之鎳基超合金T8、含12wt%鉭之鎳基超合金T12其鉭含量實測值分別為3.63、8.7及12.73wt%。 The present invention includes nickel-based superalloy T0 without added tantalum, nickel-based superalloy T4 containing 4wt% tantalum, nickel-based superalloy T8 containing 8wt% tantalum, and nickel-based superalloy T12 containing 12wt% tantalum with different tantalum contents. It is added to the method of self-compounding. Carbon content 0.01-0.05wt%, phosphorus content 0.004-0.020wt%, chromium content 17.00-21.00wt%, molybdenum content 2.50-3.10wt%, niobium content 5.20-5.80wt%, titanium content Nickel-based superalloy with content of 0.50-1.00wt%, aluminum content of 1.20-1.70wt%, cobalt content of 8.00-10.00, tungsten content of 0.80-1.40, boron content of 0.003-0.008wt%, iron content of 8.00-10.00wt%, of which nickel The content of tantalum decreases with the increase of tantalum, and it is composed of unavoidable impurities. Through vacuum induction melting, the raw materials are melted into four furnace test rods. The casting temperature of the casting parameters is 1350-1450℃, the mold temperature is 1050-1150℃, and the vacuum degree must reach 3.0×10 -2 Torr. The obtained four furnace test rods were analyzed by Spark-OES for chemical composition, and the analysis results are shown in Table 1. The results show that the total elements in the furnace test rods of the nickel-based superalloy T0 without tantalum and the furnace test rods of the nickel-based superalloy T4 with 4wt% tantalum are still within the specification values, which meet the composition specification, but the content of 8wt% tantalum The niobium element of the furnace test rod of nickel-based superalloy T8 containing 12wt% tantalum and the niobium, iron and tungsten elements of the furnace test rod of nickel-based superalloy T12 containing 12wt% tantalum all exceeded the specification, while the nickel-based superalloy containing 4wt% tantalum contained 4wt% tantalum. The measured tantalum contents of alloy T4, nickel-based superalloy T8 containing 8wt% tantalum, and nickel-based superalloy T12 containing 12wt% tantalum were 3.63, 8.7 and 12.73wt%, respectively.
接著對四爐試桿施以熱均壓(Hot isostatic pressing)及真空熱處理(Vacuum heat treatment)。熱均壓製程參數為溫度1100-1200℃、施壓1000-1100 bar持續2-4小時。而熱處理製程分為固溶熱處理及時效熱處理，其中固溶熱處理係以954-982℃的溫度範圍進行熱處理1小時後氣體冷卻(AC)至室溫；時效熱處理係以788±8℃的溫度範圍進行熱處理8小時後爐冷(FC)至704±8℃持溫8小時再爐冷至室溫。 Then, hot isostatic pressing and vacuum heat treatment were applied to the four test rods. The parameters of the hot equalizing process are the temperature of 1100-1200°C and the pressure of 1000-1100 bar for 2-4 hours. The heat treatment process is divided into solution heat treatment and aging heat treatment. The solution heat treatment is performed at a temperature range of 954-982°C for 1 hour and then gas cooled (AC) to room temperature; the aging heat treatment is performed at a temperature range of 788±8°C. After heat treatment for 8 hours, furnace cooling (FC) to 704±8°C for 8 hours and then furnace cooling to room temperature.
四爐試桿完成熱均壓與熱處理後，分別進行溫度 704℃及壓力552MPa，以及溫度704℃及壓力621Mpa之應力破斷試驗。破斷試驗遵循ASTM E139-11規範，所得應力破斷壽命如第二圖所示。無添加鉭之鎳基超合金T0合金成分符合AMS 5441規範，其在溫度704℃及壓力552MPa，以及溫度704℃及壓力621Mpa之應力破斷試驗中應力破斷壽命皆符合規範(>39小時)，而隨著鉭含量的添加，應力破斷壽命隨之增加，含8wt%鉭之鎳基超合金T8及含12wt%鉭之鎳基超合金T12之應力破斷壽命甚至長達300多小時，遠大於規範要求。更詳言之，當鉭含量為8.7-12.73wt%時，鎳基超合金經溫度704℃及壓力621MPa之應力破斷試驗所得應力破斷壽命係大於300小時。 After the hot pressure equalization and heat treatment of the test rods in the four furnaces were completed, the temperature Stress rupture test at 704℃ and pressure of 552MPa, and temperature of 704℃ and pressure of 621Mpa. The rupture test followed the ASTM E139-11 specification, and the resulting stress rupture life is shown in the second figure. The composition of the nickel-based superalloy T0 without added tantalum complies with the AMS 5441 specification, and its stress rupture life in the stress rupture test at a temperature of 704°C and a pressure of 552MPa, and a temperature of 704°C and a pressure of 621Mpa meets the specification (>39 hours) , and with the addition of tantalum content, the stress rupture life increases, and the stress rupture life of nickel-based superalloy T8 containing 8wt% tantalum and nickel-based superalloy T12 containing 12wt% tantalum is even as long as more than 300 hours. much larger than the norm requires. More specifically, when the tantalum content is 8.7-12.73wt%, the stress rupture life of the nickel-based superalloy is greater than 300 hours through the stress rupture test at a temperature of 704°C and a pressure of 621MPa.
另外，通常應力破斷壽命會以Larsen Miller Parameter作圖，如第三圖所示。Larsen Miller Parameter(LMP)=[T(℃)+273] x [20+10g(t)] x 10-3，其中T為攝氏溫度，t為破斷小時數。所得LMP之值越大，繪製出之線條位於越右側、斜率取絕對值後越小越佳。由第三圖可看出含12wt%鉭之鎳基超合金T12位於最右側，且相對於無添加鉭之鎳基超合金T0之斜率取絕對值後較小，故其應力破斷壽命表現最佳。 In addition, the stress rupture life is usually plotted against the Larsen Miller Parameter, as shown in the third figure. Larsen Miller Parameter(LMP)=[T(°C)+273] x [20+10g(t)] x 10 -3 , where T is the temperature in degrees Celsius and t is the number of hours to break. The larger the value of the obtained LMP, the more right the drawn line is, and the smaller the absolute value of the slope, the better. It can be seen from the third figure that the nickel-based superalloy T12 containing 12wt% tantalum is on the far right, and the slope is smaller than the absolute value of the nickel-based superalloy T0 without added tantalum, so its stress rupture life is the best. good.
再者，以光學顯微鏡拍攝倍率50之金相照片，如第四圖所示。各照片以截距法進行晶粒尺寸分析，即得無添加鉭之鎳基超合金T0晶粒約62.50μm，含4wt%鉭之鎳基超合金T4約59.70μm，含8wt%鉭之鎳基超合金T8約 53.8μm，含12wt%鉭之鎳基超合金T12約48.44μm，表示隨著鉭含量之添加，晶粒能逐漸細化，進而有更佳之機械性質。 Furthermore, a metallographic photograph with a magnification of 50 was taken with an optical microscope, as shown in the fourth figure. The grain size analysis of each photo is carried out by the intercept method, that is, the grain size of the nickel-based superalloy T0 without added tantalum is about 62.50 μm, the nickel-based superalloy T4 containing 4wt% tantalum is about 59.70 μm, and the nickel-based superalloy containing 8wt% tantalum is about 59.70 μm. Super alloy T8 approx. 53.8μm, the nickel-based superalloy T12 containing 12wt% tantalum is about 48.44μm, indicating that with the addition of tantalum content, the grains can be gradually refined, and thus have better mechanical properties.
以上，本發明一種提升鎳基超合金應力破斷壽命之方法，係藉由將鉭元素添加至所述碳含量0.01-0.05wt%、磷含量0.004-0.020wt%、鉻含量17.00-21.00wt%、鉬含量2.50-3.10wt%、鈮含量5.20-5.80wt%、鈦含量0.50-1.00wt%、鋁含量1.20-1.70wt%、鈷含量8.00-10.00、鎢含量0.80-1.40、硼含量0.003-0.008wt%、鐵含量8.00-10.00wt%之鎳基超合金即為商用718Plus合金，該商用718Plus合金自2004年左右發表後，因耐溫性較傳統In718優異，故廣泛應用於航太產業，例如CFM LEAP引擎中。而現今航太需求逐年上升，而本發明之鎳基合金之高溫應力破斷性能更甚於718Plus合金，故將來在產業上之應用不容小覷。 Above, a method for increasing the stress fracture life of nickel-based superalloy according to the present invention is to add tantalum element to the carbon content of 0.01-0.05wt%, phosphorus content of 0.004-0.020wt%, and chromium content of 17.00-21.00wt% , molybdenum content 2.50-3.10wt%, niobium content 5.20-5.80wt%, titanium content 0.50-1.00wt%, aluminum content 1.20-1.70wt%, cobalt content 8.00-10.00, tungsten content 0.80-1.40, boron content 0.003-0.008 The nickel-based superalloy with wt% and iron content of 8.00-10.00wt% is the commercial 718Plus alloy. Since the commercial 718Plus alloy was published around 2004, it is widely used in the aerospace industry because its temperature resistance is better than that of the traditional In718, such as in the CFM LEAP engine. Nowadays, the demand for aerospace is increasing year by year, and the high temperature stress rupture performance of the nickel-based alloy of the present invention is even better than that of the 718Plus alloy, so the application in the industry in the future should not be underestimated.
綜上所述，由於鎳基超合金廣泛應用於航太發動機之關鍵零組件中，扮演極為重要之角色，也因此航太產業需律定零件汰換週期，依時程規定汰舊換新，以確保安全性。而汰換週期主要依據使用環境與材料特性而定，若能藉由提升材料性質延長汰換週期，相對的也可使整體成本降低。本發明之效益即是藉由提升一商用鎳基超合金之應力破斷壽命，可延長至規範之五倍以上，表現出更優異之高溫穩定性且更可靠、耐用之功效。 To sum up, since nickel-based superalloys are widely used in the key components of aerospace engines and play an extremely important role, the aerospace industry needs to regulate the replacement cycle of parts, and replace the old with new ones according to the schedule. to ensure safety. The replacement cycle is mainly determined by the use environment and material characteristics. If the replacement cycle can be extended by improving the material properties, the overall cost can also be reduced. The benefit of the present invention is that by increasing the stress rupture life of a commercial nickel-based superalloy, it can be extended to more than five times the specification, showing better high temperature stability and more reliable and durable effects.
上述之實施例僅為例示性說明本創作之特點及 功效，非用以限制本發明之實質技術內容的範圍。任何熟悉此技藝之人士均可在不違背創作之精神及範疇下，對上述實施例進行修飾與變化。因此，本發明之權利保護範圍，應如後述之申請專利範圍所列。 The above-mentioned embodiments are only illustrative of the features and The effect is not intended to limit the scope of the essential technical content of the present invention. Anyone skilled in the art can modify and change the above embodiments without departing from the spirit and scope of creation. Therefore, the protection scope of the present invention should be as listed in the patent application scope described later.
S1、S2、S3:步驟 S1, S2, S3: Steps
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