• 专利附录
  • 专利说明
  • 权利要求
  • 类似技术
  • 同族专利
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  • 优先权
    • 专利摘要:
    the object of the invention is a nickel-based superalloy for a 700ºc ultra supercritical burnt coal power plant and method of manufacturing it. this nickel-based alloy comprises 0.01 ~ 0.07% dog weight, 23 ~ 25.5% dog weight, 10 ~ 14.5% dog weight, 0.3 ~ 3.5% dog weight, 0.5 ~ 2.5 % weight of w, 0.8 ~ 2.2% weight of nb, 1.0 ~ 2.5% weight of ti, 1.0 ~ 2.5% weight of al, 0.001% ~ 0.005% weight of b, 0.01 ~ 0.3% by weight of zr, 0.002 ~ 0.015% by weight of mg, less than or equal to 0.5% by weight of v, less than or equal to 0.005% by weight of la, and the balance of ni and the elements of unavoidable impurities. the present invention can effectively prevent the propagation of inter-granular cracks at elevated temperatures, and can improve impact resistance and also creep resistance of the alloy.
    公开号:BR112015031328B1
    申请号:R112015031328
    申请日:2014-04-16
    公开日:2020-01-28
    发明作者:Xishan Xie；Fusheng Lin；Shuangqun Zhao
    申请人:University Of Science And Technology Beijing；Shanghai Power Equipment Research Institute；
    IPC主号:
    专利说明:

    NICKEL-BASED SUPERLINK FOR ULTRA SUPERCRITICAL BURNED COAL ENERGY PLANT 700 ° C AND MANUFACTURING METHOD ”
    Descriptive Report
    The present invention belongs to the technical field of the nickel-based superalloy, in particular to a nickel-based superalloy for the 700 ° C ultra supercritical burnt coal power plant. This new superalloy can be applied as the high temperature components in ultra supercritical coal-fired power plants at 700C steam temperature. The higher temperatures of the new service alloy can be reached at 800C.
    The scarcity of energy supply and the deterioration of the environment have become the main factors to restrict the sustainable development of the economy, society and the environment worldwide. Electricity, as a secondary energy, will still take a leading position in the energy consumption market for quite a long time to come. In the structure of electric power generation, thermal power generation occupies a leading position in most countries in the world, which will not be changed for long in the future. Currently, most coal-fired power plants in the world are sub-critical plants with a steam parameter in the range of 538 ° C / 18.5MPa. However, from the end of the century
    Petition 870150006884, of 12/14/2015, p. 6/58
    2/45 last, supercritical plants with a range of 566 ° C / 24MPa and ultra supercritical power plants with a range of 600C / 27MPa take a major position in the development of coal-fired thermoelectric plants. The thermal efficiency of power plants has been improved from about 35% for subcritical units to about 45% for ultra supercritical units. This plays an important role in saving coal and reducing the emission of pollutants, such as SOx, NOx and CO2. However, in recent decades, major developed countries and unions in countries around the world, for example, the EU, the USA and Japan, have implemented research and development on 700 ° C 700C ultra-critical burnt coal power generation technologies (or 760C) in succession.
    The EU is the first to start this project in 1998, increasing the steam temperature to 700C / 720C / 35MPa, with the expected efficiency of power generation increasing from the current 45% to more than 50%. The USA and Japan then started similar study projects in the early 21st century. In 2011, China also began to research and develop energy generation technologies powered by 700C ultra supercritical coal. In the structure of Chinese electric power generation, the thermal units take a position up to 80%, while the average consumption of coal from the plants is much higher than that of the
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    3/45 developed countries in the world. To reduce coal consumption by increasing the steam parameter of coal-fired power plants, not only will coal resources be saved and reduced CO2 emissions, etc., but it will also be significant for the sustainable development of the economy, society and the economy. environment.
    As the temperature and pressure of the coal-fired power generating units are
    increased to the track 7 0 0 ° C / 72 0 ° C / 35MPa, the requirements more high are taxes on force and resistance The corrosion in key components of high temperature of power plants in energy, for example, the HP rotors and IP, cylinders and shell valves in
    turbines, super heaters and reheaters in boilers, heads and steam tubes, etc. Generally, the temperature of the outer wall of the superheater and reheater tubes in the boilers is about 50 ° C higher than the internal steam temperature. Therefore, when the steam temperature in the superheater and reheater tubes reaches 700C and 720C, the maximum temperature of the outer walls of the tubes can reach around 770C and even higher. At the same time, the vapor pressure in the tubes is also increased. With this temperature and vapor pressure, steel and austenitic 9 ~ 12Cr% steels, such as Super304H and HR3C, which are widely applied in ultra supercritical coal-fired power plants, do not meet the requirements for
    Petition 870150006884, of 12/14/2015, p. 8/58
    4/45 strength and corrosion resistance, therefore nickel-based superalloys should be used.
    Currently, for nickel-based alloys used in civil works (for example, the petrochemical industry), corrosion resistance and high temperature properties are required to be considered in the oxidation or reduction environment. However, for some age-hardening nickel-based alloys applied to the aerospace field, the duration of the alloys is relatively short and the high temperature resistance requirements are more important. Due to the large difference in the purposes, namely, the prominent characteristics of the extended operating time (30-40 years) of ultra supercritical power plants, the current nickel-based super alloys generally do not meet the requirements for high temperature resistance, temperature maximum service, structure stability and oxidation / sulfur resistance at the same time and thus no longer meets the requirements for long term use by the high temperature components of the 700C ultra supercritical coal power plants. The EU studied the nickel-based alloys Inconel 617 and Nimonic 263 in the ultra supercritical power generation program 700C, obtained alloy 617B by optimizing the composition of alloy 617 and is now optimizing alloy 263. The Japanese company Sumitomo has developed the alloy HR6W alloy based
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    Fe-Ni. The Swedish company Sandvik also developed the austenitic alloy Sanicro25 based on Fe-Ni. These alloys do not all meet the component requirements of the highest temperature. For the EU's ultra supercritical 700 ° C plane, SMC developed the Inconel 740 alloy which has obvious characteristics of high strength and high resistance to corrosion and thus became the main candidate materials for the high temperature parts of the power units. China is also actively exploring alloys for use at higher temperatures on the basis of the nickel-iron alloy GH2984, which was originally used as the super heater for marine boilers. So far, the aforementioned alloys are still under development.
    Based on the results of the influence of elements, such as Co, Cr, Mo, W, Al, Ti, Nb and C on structures and properties, a comprehensive analysis of the reasonable combination of reinforcement and precipitation, solid solution and precipitation reinforcement of alloys and by means of good grain boundary reinforcement, the present invention obtains a nickel-based alloy capable of being used for a long time at a temperature below 800 ° C. It has high ambient temperature and extensible high temperature properties, high temperature breakage properties and excellent corrosion resistance. It has great prospects for the application of 700C ultra supercritical coal power plants.
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    The objective of the present invention is to provide a nickel-based superalloy for the 700C ultra supercritical coal power plants and a method of manufacturing it. The new nickel-based superalloy has the advantages of a reasonable combination of chemical compositions, hot deformation properties, excellent mechanical properties of high temperature and corrosion resistance, and good structure stability.
    To fulfill the aforementioned objective, the present invention provides a nickel-based superalloy for 700C ultra supercritical coal power plants, characterized by comprising: C
    0.01 ~ 0.07% weight, Cr 23 ~ 25.5% weight, Co 10 ~ 14.6% weight, Mo 0.3 ~ 3.5% weight, W 0.5 ~ 2.5% weight, Nb 0.8 ~ 2.2% weight , Ti 1.0 ~ 2.5% by weight, Al 1.0 ~ 2.5% by weight, B 0.001% ~ 0.005 by weight, Zr 0.01 ~ 0.3% by weight, Mg 0.002 ~ 0.015% by weight, V 0.01 ~ 0.5% by weight, La 0.001 ~ 0.005% by weight, the balance of Ni and elements of unavoidable impurities, including S <0.010% by weight, P <0.015% by weight, Si <0.3% by weight and Mn <0.5% weight, where the index (Al / (Ti + Nb)) of the atomic percentage of Al to the sum of the atomic percentage of Ti and Nb is in the range of 1.0-1.3; the sum of the atomic percentages of Al, Ti and Nb is 5.5-6.2in%; the (Cr / (Mo + W)) index of the atomic percentage of Cr for the sum of the atomic percentage of Mo and W is greater than 12 and the sum of the atomic percentages of Cr, Mo and W is not greater than 30%.
    In addition, the percentage of
    Petition 870150006884, of 12/14/2015, p. 11/58
    7/45 reinforcement of precipitated time □□ of the nickel-based superalloy for the 700C ultra supercritical coal power plants is 14 ~ 19% by weight.
    The present invention also provides a nickel-based superalloy manufacturing method for 700C ultra supercritical coal power plants, characterized by including the following steps:
    Step 1: Put 0.01 ~ 0.07% C weight, 23 ~ 25.5% Cr weight, 10 ~ 14.6% Co weight, 0.3 ~ 3.5% Mo weight, 0.5 ~ 2.5% weight W, 0.8 ~ 2.2% Nb weight, 1.0 ~ 2.5% Ti weight, 1.0 ~ 2.5% Al weight, 0.001 ~ 0.005% B weight, 0.01 ~ 0, 3% by weight of Zr, 0.01 ~ 0.5% by weight of V, 48-58% by weight of Ni in a vacuum induction furnace, maintaining the index of (Al / (Ti + Nb)) of atomic percentage of Al for the sum of the atomic percentage of Ti and Nb in the range of 1.0-1.3, the sum of the atomic percentages of Al, Ti and Nb in the range of 5.5-6.2in%, the index of (Cr / (Mo + W)) of the atomic percentage of Cr for the sum of the atomic percentage of Mo and W is greater than 12. The sum of the atomic percentages of Cr, Mo and W is not greater than 30%. In the meantime, feed 3-6% by weight of dry auxiliary materials with a purity level greater than 99.5% for the vacuum induction furnace and auxiliary materials consisting of 40% by weight of CaF2, 40% by weight of CaO and
    20% by weight of Al2O3. Melt these raw materials in the vacuum induction furnace to a vacuum condition of not less than 10-3Bar. After the raw materials are
    Petition 870150006884, of 12/14/2015, p. 12/58
    8/45 completely melted, refine the molten metal for more than 30 min to remove the gases, keeping the vacuum at 10-3Bar. After refining, charge shielding gas with Argon (Ar) until the pressure reaches 0.4 bar, adding 0.3-0.6% weight of Ni-20Ca alloy at the same time, to remove the harmful impurity element S, where the temperature of the molten alloy is not less than 1,500C. Add 0.01 ~ 0.025% weight of Ni-20Mg alloy and 0.001 ~ 0.005% weight of La metal instead of performing desulfurization and purification. Totally melt the materials, mixing the molten metal well, filtering the molten metal and moistening the molten metal into the mold, the alloy ingot will form an Argon atmosphere.
    Step 2: perform diffusion, forging, solid-solution annealing and aging treatment of the alloy to obtain the nickel-based superalloy for the 700C ultra supercritical coal power plants.
    Preferably in step 2, the diffusion annealing temperature is applied at 1,150 ~ 1,220 ° C, and the duration is 16 ~ 48 h.
    Preferably, in step 2, the forging temperature is not less than 1.050 C.
    Preferably, in step 2, the temperature of the solid solution treatment is applied to
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    1,100 ~ 1,200 ° C and the duration is 0.5 ~ 2h.
    Preferably, in step 16, the temperature of the aging treatment is carried out at 800 ° C and the duration is 4 ~ 16h.
    Preferably, in step 2, before diffusion annealing, the alloy ingot is refined again, by vacuum arc remelting or by electro-slag remelting in a shielding gas atmosphere.
    More preferably, if the vacuum arc re-melting method is employed in step 2, the re-melting rate must be strictly controlled to be less than 300 kg / h.
    More preferably, when remelting electro-slag in a shielding gas atmosphere is used in step 2, a purified complex quinary slag system is used. The purified complex quinary slag system comprises 40 ~ 45 wt% CaF2, 20 ~ 30 wt% Al2O3, 15 ~ 20 wt% CaO, 5 ~ 10 wt% MgO and 5-10 wt% TiO2 . The purified complex quinary slag system must be extracted to ensure SiO2 <0.5%, and must be cooked for 4 hours at a temperature of 800C before use. Using (40 ~ 45% CaF2 + 20 ~ 30% Al2O3 + 15 ~ 20% CaO + 5 ~ 10% MgO + 5 ~ 10% TiO2 can guarantee stable A1, Ti and Mg ingredients.
    The content tracks of the composition
    Petition 870150006884, of 12/14/2015, p. 14/58
    10/45 chemistry of the main alloy elements of the high-temperature nickel-based alloy of the present invention, including Ni, Cr, Co, Mo, W, Nb, Ti, Al, B, Zr, Mg, V, La and some impurity elements S, P, Si, Mn, etc., which are inevitable in the industrial production process mentioned above. In addition, the content of microelements of harmful impurities, such as Pb, Sn, As, Sb and Bi must be strictly controlled according to current industrial protection technologies because these microelements are harmful to the forging process and durability as well as the high temperature plasticity of the alloy.
    The reasons for limiting the chemical composition of this nickel-based super alloy for 700C ultra supercritical coal power plants in the above mentioned ranges are, respectively, described below.
    C, as a reinforcing element, is good for the high temperature breaking strength of the alloy when the M23C6 carbide is formed at the grain boundaries and when C with a content of less than 0.01%, it is not sufficient to form a certain amount of M23C6. C together with Ti and Nb can form a primary MC carbide, good for controlling grain size. In the case of excessive C content, more Ti and Nb will be consumed to form MC, so the C content must be kept below 0.06%. In addition, C also has the function of ensuring
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    11/45 mobility of molten metal during casting.
    Cr is an important element to improve resistance to oxidation and corrosion and the high temperature resistance of the nickel-based alloy is also a major element for the formation of carbides at the grain boundaries. Research has shown that, under the condition that the inside of the boiler tubes is filled with high temperature steam, in the alloy, Cr with a content greater than 23% can form a protective film of oxide Cr2O3 on the inner wall of the tube and can ensure that the outer wall of the pipe is resistant to flue gas corrosion at the same time. Excessive Cr content will affect the stability of the alloy's structure and functionality so that the Cr content is not required to exceed 25.5%.
    Co is beneficial to nickel-based alloy resistance at a high temperature and high temperature corrosion resistance. Co in the Ni-Cr solid solution can reduce the lack of stacking energy and plays a good role in strengthening the solid solution. When the CO content is less than 10%, resistance to high temperature is reduced. However, Co is a strategic element with a high price. Excessive Co enables the formation of the η phase in the alloy, which is detrimental to the properties of the alloy and affects the forgeability of the alloy. Therefore, the CO content is limited in the range of 10.0 ~ 14.6%. For this
    Petition 870150006884, of 12/14/2015, p. 16/58
    12/45 invention, is an important factor to rationally control the reinforcement elements and reduce the cost of the alloy.
    Mo when entering the matrix □ of the nickel-based alloy plays an important reinforcing role in the solid solution. In particular, in the condition of reducing the CO content to weaken the strength of the solid solution, the use of Mo to reinforce the solid solution is also one of the characteristics of the reinforcing element of the present invention. However, when excess Mo is added, which is obviously not only detrimental to the alloy's resistance to corrosion of flue gases in the environment from the burnt coal, but also promotes the formation of the σ phase and reduces functionality the hot. Therefore, the Mo content is controlled to be 0.3 ~ 3.5%.
    W enters the De matrix in the □□ strengthening phase by half, respectively. W has a relatively large atom radius that is greater than the radius of the Ni matrix element by more than ten percent and plays an obvious role in reinforcing the solid solution. In particular, W and Mo added together reinforce the solid composite solution. However, W is an element to accelerate thermal corrosion and therefore the W content is controlled to be 0.5 ~ 2.5%.
    The Nb content is controlled to stay at 0.8 ~ -2.2%. The difference between the rays of the atoms of
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    Nb and Ni is higher than that of the atoms of W and Ni. Nb is an important precipitation reinforcer and the reinforcing element in the solid solution in the alloy of the present invention and, together with Al and Ti are reinforcing elements in the phase. However, the Nb content must be controlled to be appropriate because the excessive Nb promotes the formation of the η phase, reduces the protective properties of the oxide film and deteriorates the welding property due to the promotion of liquid cracks.
    Ti is controlled to be 1.0 ~ 2.5%. It is an important reinforcement element for the formation of the □□ phase. The Ti element is also an important grain stabilizer, together with the primary forming carbide Nb (Ti, Nb) C. However, an excessive content of Ti promotes the formation of the harmful η phase and causes internal oxidation, reducing the plasticity of the alloy.
    Al is good for resisting oxidation and improving the structure of the oxide film, together with Ti and Nb forming the □□ reinforcement phase with Ni. Al is an important element for the stabilization of the □□ phase and restricts the formation of the η phase. A low content of Al causes an undesirable reinforcing effect and reduces the high temperature force; while a high Al content obviously reduces the plasticity and strength of the alloy and reduces the extent of the alloy's processing temperature. However, in a high temperature environment of
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    14/45 sulfurization, a high Al content promotes internal oxidation and internal sulfurization corrosion. Therefore, Al is limited in the range of 1.0 ~ 2.5%.
    B is a micro-alloy element, rich in grain boundaries, reinforcing the bond strength of the grain boundaries. Boride at the grain boundary can prevent the grain boundary from slipping, cavity connection and crack propagation, it has an obvious effect of strengthening the crawling property of the alloy. There is an optimum B content. In the present invention, the B content in the alloy is controlled to be 0.001 ~ 0.005%.
    Zr is controlled to stay at 0.010.3%, good for purifying the grain boundaries and reinforcing the bond strength of the grain boundaries and together with B it is good for maintaining the high temperature strength and resistance to plasticity of the alloy. Excessive Zr reduces hot functionality. Another effect of Zr is, of course, to increase the adhesion property of the protective oxide film on the alloy surface.
    Mg is added as a micro-alloy element. The appropriate Mg is good for improving the life and plasticity of the alloy. The segregation of Mg at the grain boundary and phase boundaries can reduce the grain boundary energy and the boundary energy between phases, improve the precipitation morphology of the second phase and reduce the local stress concentration. In addition, Mg can also be combined with impurity elements to
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    15/45 purify the grain boundaries. Mg is controlled to stay at 0.004 ~ 0.015%.
    V, when distributed in matrix □, can effectively increase the deformation of the structure and increase the strength of the solid solution. However, a part of V also enters the □ 'strengthening phase to replace Al. V can also easily form precipitated, good and dispersive VC during solidification, it is good for refining grains. In addition, V can improve the plasticity of the alloy's thermal functionality and is controlled to be at 0.001 ~ 0.5% by weight.
    La is added as a micro-alloy element and can be combined with impurity elements, in particular the harmful element S, to play the role of purifying and strengthening the grain boundaries. In addition, La is good for oxidation resistance. It is controlled to stay at 0.001 ~ 0.005%.
    S is an element of harmful impurity, leading to the segregation of elements and the formation of a harmful phase during solidification. In the alloy, S is segregated at the grain boundaries and at the boundaries between the phases, seriously affecting thermal plasticity and the high temperature breaking properties of the alloy. The S is controlled below 0.010% and must be controlled to be as low as possible.
    P has a double effect, leading to element segregation and phase precipitation
    Petition 870150006884, of 12/14/2015, p. 20/58
    16/45 harmful during solidification. Adequate P content can improve the crawl property. Excessive P is seriously segregated at the grain boundary to reduce the strength of the grain boundary and affect strength. The P must be controlled to be below 0.015%.
    Si is an element of common impurity, rich in the grain boundaries. It can reduce the grain boundary force and promote the formation of the TCP phase. The research results of the present invention indicate that a high Si content can promote precipitation of the Si-rich G phase at the grain boundary to obviously affect the plasticity, toughness and functionality of the alloy. In this way Si must be controlled below 0.3%.
    Mn, like other impurities, is secreted at the grain boundaries. Mn can weaken the boundary strength of the grain, reduce creep resistance and promote the formation of the harmful phase at the grain boundaries. Mn must be controlled below 0.5%.
    Ni is the most important element of the matrix De the main element of formation of the □□ step of precipitation reinforcement. To guarantee the stability of the structure, obtain resistance to high temperatures and stiffness and ensure that the alloy has good functionality, the Ni content must be maintained at around 50%.
    Figure 1 is a diagram of the research result on the relationship between the amount of precipitation
    Petition 870150006884, of 12/14/2015, p. 21/58
    17/45 and the content of Al + Ti + Nb. According to the design of the alloy composition of the present invention, the principles of controlling the reinforcement precipitation phase Al, Ti and Nb focus on: the Al / (Ti + Nb) index is in the range of 1.0-1, 3, and the sum of Al + Ti + Nb is 5.5 ~ 6.2%, so that the precipitation of the reinforcement phase is in the range of 14 ~ 19% by weight. Forming the effect of reinforcing adequate precipitation is the first guarantee factor to obtain a high adequate resistance without phase □□ for the transformation of phase □. The structure of the reinforced precipitation phase of the alloy is stable.
    invention is of the Ni3 type (Al, Ti, Nb). Although Nb and Ti have good reinforcing effects at a temperature of 700-800C, a large coherent stress field is generated due to a large degree of □□ / □ incompatibility, so this □□ phase is metastable. It is also easy to form the η phase of the Ni3 type (Ti, Nb). In the condition of reasonable control in relation to the compositions and using the method of fusion technology, billet forging and heat treatment method, the present invention ensures that the □□ phase is precipitated in a favorable position in the grains and in the grain boundaries during the heat treatment. This makes the discontinuous distribution characteristics of □□ at the grain boundaries, preventing the spread of cracks along the grain boundaries, and improves the impact resistance and creeping properties of the alloy.
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    This is a notable feature of the structure design of the present invention to improve the □□ phase stability and optimize the phase reinforcement effect. Figure 2 is a microstructure diagram of the alloy of the present invention after heat treatment.
    In the design of the alloy composition of the present invention, the principle of controlling the element Mo and Cr is as follows: the atomic index of Cr / (Mo + W) is greater than 12, and the sum of Mo + Cr + W is not exceeds 30%. In a long-term aging process at a temperature of 700-800C, there is no □ phase and □ phase formed in this alloy and the impurity element Si content is controlled below 0.3% by weight to limit precipitation of phase G. The microstructures in the standard state of heat treatment and after long-term aging of the alloy can be seen in the figure attached to the summary and in figure 2, respectively.
    In conclusion: the present invention takes into account not only the rational combinations of the reinforcement of the solid solution composed of an appropriate amount of W in the Ni-Cr-Co-Mo matrix combined with reinforcement of the precipitation of Al, Ti and Nb, but also the addition of a small amount of vanadium to improve the reinforcement and optimization of micro-alloy elements B, Zr and Mg. The present invention is to strictly control the contents of conventional elements harmful S, P, Si and Mn, in particular, and the addition of a
    Petition 870150006884, of 12/14/2015, p. 23/58
    19/45 La trace in the fusion process, and therefore it plays the role of purifying and strengthening the grain boundaries. The chemical composition design of the alloy is more rational; the microstructure has a high stability during long-term aging. The reinforcement of the precipitation phase □□ 14 ~ 19% weight is generated and the precipitation of harmful phases, such as phase η, phase G and phase σ are contained in the aging process. The □□ phase in the alloy is of the Ni3 type (Al, Ti, Nb) and the sum of Al, Ti and Nb, and the Al / (Ti + Nb) index are rationally controlled to obtain the appropriate amount of the reinforcement stable. It accompanies the corresponding purified fusion process, the reasonable bill forging method and heat treatment method, the □□ phases are precipitated in the grains and also in favorable positions of the grain boundaries, capable of effectively preventing the propagation of cracks
    intergranular and improve hardness of the impact and properties of crawling them. Figure 1 is a result diagram of research of the relationship at amount in precipitation □□ and content of Al + Ti + Nb. Figure 2 it is a diagram in
    alloy microstructure after long-term aging.
    Figure 3 is a TTT diagram of the precipitation phase η of alloy 2 from a comparative example.
    Figure 4 is a TTT diagram of the phase
    Petition 870150006884, of 12/14/2015, p. 24/58
    20/45 precipitation σ of alloy 3 in a comparative example.
    The figure attached to the summary is a microstructure diagram of this alloy in a standard heat treatment state.
    To make the present invention easily understandable, the invention is described in detail in combination with the following preferred embodiments and comparative examples.
    In a first embodiment, the nickel-based super alloy for the 700C ultra supercritical coal power plants comprises C, Cr, Co, Mo, W, Nb, Ti, Al, B, Zr, Mg, V, La, Ni and the elements of unavoidable impurities. The weight percentages actually tested for chemical compositions and the weight percentages of the impurities S, P, Si and Mn can be seen in table 1. The (Al / (Ti + Nb)) index of the atomic percentage of Al for the sum of the atomic percentage of Ti and Nb, the sum of (Nb + Ti + Al) of the atomic percentages of Al, Ti and Nb, the index (Cr / (Mo + W)) of the atomic percentage of Cr and the sum of Mo and W atoms, and the sum (Cr + Mo + W) of the atomic percentages of Cr, Mo and W can be seen in Table 1.
    A method of manufacturing this nickel-based superalloy for the 700C ultra supercritical coal power plants comprises the following steps:
    Select high-quality raw materials
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    quality, put on 0.05% weight gives C, 24.3% weight in Cr, 14.2% weight in Co, 0.32% weight in Mo, 1.05% weight in W, 1.48% weight in Nb, 1. 52% weight of You, 1.61% by weight in Al, 0.003% weight in B, 0. 02% weight of Zr, 0.18% V weight, 55% Weight
    Ni and 5% by weight of dry auxiliary materials with a purity of 99.5% for a vacuum induction oven, auxiliary materials consist of 40% by weight of CaF2, 40% by weight of CaO and 20% by weight of Al2O3. These raw materials are melted in the vacuum induction furnace under vacuum conditions of 10-3Bar. After the raw materials are completely melted, the molten metal is refined for 10 minutes to remove the gases, keeping the vacuum no lower than 10-3Bar. After refining is complete, charge the Argon gas until the pressure reaches 0.4 bar, adding 0.5% by weight of Ni20Ca alloy at the same time to remove the harmful impurity element S. When the temperature of the molten metal is at 1520 ° C before pouring; add 0.015% by weight of Ni-20mg alloy and 0.005% by weight of La metal instead of performing desulfurization and purification. To fully melt the materials, mixing the molten metal well, filtering the molten metal and pouring the molten metal into the molds, the alloy ingot will form in an Argon atmosphere.
    Carry out diffusion annealing to the alloy ingot at a temperature of 1,190C and forging billets at a temperature of 1,200C, forging
    Petition 870150006884, of 12/14/2015, p. 26/58
    22/45 the alloy ingot in 15mm bar product □ for reheating three times, implement a solution treatment of the solid product in bar for 1 h at a temperature of 1.150C, cool the water and age the product in bar for 16 hours at a temperature of 800C, cool the air. In this way, the weight fraction of the □□ reinforcement phase of this nickel-based super alloy for the 700C ultra supercritical coal power plants is 16.8% by weight.
    In a second embodiment, the nickel-based superalloy for the 700C ultra supercritical coal power plants comprises C, Cr, Co, Mo, W, Nb, Ti, Al, B, Zr, Mg, V, La , Ni and the elements of unavoidable impurities. The weight percentages actually tested for chemical composition and the weight percentages of the impurities S, P, Si and Mn can be seen in table 1.
    The (Al / (Ti + Nb)) index of the atomic percentage of Al to the sum of the atomic percentage of Ti and Nb, the sum of (Nb + Ti + Al) of the atomic percentages of Al, Ti and Nb, the index (Cr / (Mo + W)) of the atomic percentage of Cr and the sum of Mo and W, and the sum (Cr + Mo + W) of the atomic percentages of Cr, Mo and W can also be seen in table 1.
    The manufacturing method of this nickel-based super alloy for the 700C ultra supercritical coal power plants comprises the
    Petition 870150006884, of 12/14/2015, p. 27/58
    23/45 following steps:
    Select high-quality raw materials
    quality and put 0.05% weight in Ç, 24 .5% weight in Cr, 10.2% weight in Co, 1.35% weight in Mo, 1. 05% weight in W, 1,678% weight in Nb, 1.49% weight of You, 1, 72% by weight in Al,
    0.003% weight of B, 0.02% weight of Zr, 0.17% weight of V, 57% weight of Ni and 5% weight of dry auxiliary materials with a purity of 99.5% for a vacuum induction furnace. Auxiliary materials consist of 40 wt% CaF2, 40 wt% CaO and 20 wt% Al2O3. These raw materials are melted in the vacuum induction furnace under vacuum conditions of 10-3Bar. After the raw materials are completely melted, the molten metal is refined for 10 minutes to remove the gases, keeping the vacuum no lower than 10-3Bar. After refining is complete, load with Argon gas until the pressure reaches 0.4bar, adding 0.5% by weight of Ni20Ca alloy at the same time to remove the harmful impurity element S. When the temperature of the molten metal is at 1520 ° C before pouring; add 0.015% by weight of Ni-20mg alloy and 0.005% by weight of La metal instead of performing desulfurization and purification. To fully melt the materials, mixing the molten metal well, filtering the molten metal and pouring the molten metal into the molds, the alloy ingot will form in an Argon atmosphere.
    Perform diffusion annealing
    Petition 870150006884, of 12/14/2015, p. 28/58
    24/45 for the alloy ingot at a temperature of 1,190C and forging billets at a temperature of 1,200C, forging the alloy ingot in a 15mm bar product □ for three times reheating, implementing a product treatment solution solid bar for 1 h at a temperature of 1.150C, cool the water and age the product in a bar for 16 hours at a temperature of 800C, cool the air. In this way, the weight fraction of the □□ reinforcement phase of this nickel-based superalloy for the 700C ultra supercritical coal power plants is 18.5% by weight.
    In a third embodiment, the nickel-based superalloy for the 700C ultra supercritical coal power plants comprises C, Cr, Co, Mo, W, Nb, Ti, Al, B, Zr, Mg, V, La, Ni and the elements of unavoidable impurities. The weight percentages actually tested for chemical composition and the weight percentages of the impurities S, P, Si and Mn can be seen in table 1. The (Al / (Ti + Nb)) index of the atomic percentage of Al for the sum of the atomic percentage of Ti and Nb, the sum of (Nb + Ti + Al) of the atomic percentages of Al, Ti and Nb, the index (Cr / (Mo + W)) of the atomic percentage of Cr and the sum of Mo and W, and the sum (Cr + Mo + W) of the atomic percentages of Cr, Mo and W can also be seen in Table 1.
    The manufacturing method of this nickel-based super alloy for power plants in the
    Petition 870150006884, of 12/14/2015, p. 29/58
    25/45 700% ultra supercritical coal comprises the following steps:
    Select high-quality raw materials
    quality and put on 0.05% weight in Ç, 24 .7% weight in Cr, 14.5% weight in Co, 2. 43% weight in Mo, 1. 15% weight in W, 1.62% weight in Nb, 1.56 % weight of You, 1.56% by weight in Al,
    0.002% weight of B, 0.04% weight of Zr, 0.10% weight of V, 52% weight of Ni and 5% weight of dry auxiliary materials with a purity of 99.5% for a vacuum induction furnace. Auxiliary materials consist of 40 wt% CaF2, 40 wt% CaO and 20 wt% Al2O3. These raw materials are melted in the vacuum induction furnace under vacuum conditions of 10-3Bar. After the raw materials are completely melted, the molten metal is refined for 10 minutes to remove the gases, keeping the vacuum no lower than 10-3Bar. After refining is complete, load with Argon gas until the pressure reaches 0.4 bar, adding 0.5% by weight of Ni20Ca alloy at the same time to remove the harmful impurity element S. When the temperature of the molten metal is at 1520% before pouring; add 0.015% by weight of Ni-20mg alloy and 0.005% by weight of La metal instead of performing desulfurization and purification. To fully melt the materials, mixing the molten metal well, filtering the molten metal and pouring the molten metal into the molds, the alloy ingot will form in an Argon atmosphere.
    Petition 870150006884, of 12/14/2015, p. 30/58
    26/45
    Carry out diffusion annealing for 24 hours in the alloy ingot at a temperature of 1,190% and forging billets at a temperature of 1,200%, forging the alloy ingot in a 15mm bar product □ for three times the reheating, implement a solution of treating the solid product in a bar for 1 hour at a temperature of 1.150%, cooling the water and aging the product in a bar for 16 hours at a temperature of 800%, cooling the air. Thus, the weight fraction of the □□ reinforcement phase of this nickel-based superalloy for 700% ultra supercritical coal power plants is 17% by weight.
    In a fourth embodiment, the nickel-based superalloy for 700% ultra supercritical coal power plants comprises C, Cr, Co, Mo, W, Nb, Ti, Al, B, Zr, Mg, V, La , Ni and the elements of unavoidable impurities. The weight percentages actually tested for chemical composition and the weight percentages of the impurities S, P, Si and Mn can be seen in table 1.
    The (Al / (Ti + Nb)) index of the atomic percentage of Al to the sum of the atomic percentage of Ti and Nb, the sum of (Nb + Ti + Al) of the atomic percentages of Al, Ti and Nb, the index (Cr / (Mo + W)) of the atomic percentage of Cr and the sum of Mo and W atoms, and the sum (Cr + Mo + W) of the atomic percentages of Cr, Mo and W can also be seen in table 1.
    Petition 870150006884, of 12/14/2015, p. 31/58
    27/45
    The manufacturing method of this nickel-based superalloy for 700 ° C ultra supercritical coal power plants comprises the following steps:
    Select high-quality raw materials
    quality and put 0.07% weight of C, 25.0% weight in Cr, 14.6% weight in Co, 2.87% weight of Mo, 1.20% weight in W, 1.56% weight in Nb, 1.60% Ti weight, 1.58% by weight in Al, 0.002% weight in B, 0.04% Zr weight, 0 .15% V weight, 51% weight Ni and 5% in weight of dry auxiliary materials with an purity of 99, 5% for an oven vacuum induction and the
    auxiliary materials consisting of 40 wt% CaF2, 40 wt% CaO and 20 wt% Al2O3. These raw materials are melted in the vacuum induction furnace under vacuum conditions of 10-3Bar. After the raw materials are completely melted, the molten metal is refined for 10 minutes to remove the gases, keeping the vacuum no lower than 10-3Bar. After refining is complete, load with Argon gas until the pressure reaches 0.4bar, adding 0.5% by weight of Ni20Ca alloy at the same time to remove the harmful impurity element S. When the temperature of the molten metal is at 1520C before pouring; add 0.015% by weight of Ni-20mg alloy and 0.005% by weight of La metal instead of performing desulfurization and purification. Fully melt the materials, mixing the molten metal well, filtering the molten metal and pouring the molten metal inside
    Petition 870150006884, of 12/14/2015, p. 32/58
    28/45 of the molds, the alloy ingot will form in an argon atmosphere.
    Carry out diffusion annealing for 24 hours in the alloy ingot at a temperature of 1,190C and forging billets at a temperature of 1,200C, forging the alloy ingot in a 15mm bar product □ for three times the reheating, implement a solution of treating the solid product in a bar for 1 hour at a temperature of 1.150C, cooling the water and aging the product in a bar for 16 hours at a temperature of 800C, cooling the air. This way, the weight fraction of the □□ reinforcement phase of this nickel-based superalloy for the 700C ultra supercritical coal power plants is 17.3% by weight.
    In a fifth embodiment, the nickel-based superalloy for the 700C ultra supercritical coal power plants comprises C, Cr, Co, Mo, W, Nb, Ti, Al, B, Zr, Mg, V, La, Ni and the elements of unavoidable impurities. The weight percentages actually tested for chemical composition and the weight percentages of the impurities S, P, Si and Mn can be seen in table 1. The (Al / (Ti + Nb)) index of the atomic percentage of Al for the sum of the atomic percentage of Ti and Nb, the sum of (Nb + Ti + Al) of the atomic percentages of Al, Ti and Nb, the index (Cr / (Mo + W)) of the atomic percentage of Cr and the sum of Mo and W, and the sum (Cr + Mo + W) of the atomic percentages
    Petition 870150006884, of 12/14/2015, p. 33/58
    29/45 of Cr, Mo and W can also be seen in table 1.
    The manufacturing method of this nickel-based superalloy for the 700C ultra supercritical coal power plants comprises the following steps:
    Select high quality raw materials and place 0.06% C weight, 24.4% Cr weight, 13.6% Co weight, 3.04% Mo weight, 1.16% W weight, 1.51% Nb weight, 1.51 % weight of Ti, 1.51% weight of Al, 0.003% weight of B, 0.05% weight of Zr, 0.16% weight of V, 52% weight of Ni and 0.5% weight of materials dry auxiliaries with a purity of 99.5% for a vacuum induction furnace and auxiliary materials consisting of 40% by weight of CaF2, 40% by weight of CaO and 20% by weight of Al2O3. These raw materials are melted in the vacuum induction furnace under vacuum conditions of 10-3Bar. After the raw materials are completely melted, the molten metal is refined for 10 minutes to remove the gases, keeping the vacuum no lower than 10-3Bar. After refining is complete, load with Argon gas until the pressure reaches 0.4bar, adding 0.5% by weight of Ni20Ca alloy at the same time to remove the harmful impurity element S. When the temperature of the molten metal is at 1520C before pouring; add 0.020% by weight of Ni-20Mg alloy and 0.005% by weight of La metal instead of performing desulfurization and purification. Fully melt the materials, mixing the molten metal well, filtering the
    Petition 870150006884, of 12/14/2015, p. 34/58
    30/45 molten metal and pouring molten metal into the molds, the alloy ingot will form in an argon atmosphere.
    Refuse the molten alloy ingot in the vacuum induction furnace by vacuum arc remelting. Anneal the electrode for 1 hour at a temperature of 900 C; remove the oxide layer on the surface; weld the electrode to a vacuum of 10-3mmHg; control the vacuum to stay at 10-3mmHg; keep the melting index at 250kg / h; and finally annealing the alloy ingot for 1 hour at a temperature of 900C;
    Carry out diffusion annealing in the remelted alloy ingot at a temperature of 1.190C and forging billet at a temperature of 1,200C, forging the alloy ingot in a 15mm bar product □ for three times the reheating, implement a solution treatment solid product bar for 1h at a temperature of 1.150C, cool the water and age the product bar for 16 hours at a temperature of 800C, cool the air. In this way, the weight fraction of the □□ reinforcement phase of this nickel-based superalloy for the 700C ultra supercritical coal power plants is 15% by weight.
    In a sixth form of Realization, the nickel-based super alloy for the 700C ultra supercritical coal power plants comprises C, Cr, Co,
    Petition 870150006884, of 12/14/2015, p. 35/58
    31/45
    Mo, W, Nb, Ti, Al, B, Zr, Mg, V, La, Ni and the elements of unavoidable impurities. The weight percentages actually tested for chemical composition and the weight percentages of the impurities S, P, Si and Mn can be seen in table 1.
    The (Al / (Ti + Nb)) index of the atomic percentage of Al to the sum of the atomic percentage of Ti and Nb, the sum of (Nb + Ti + Al) of the atomic percentages of Al, Ti and Nb, the index (Cr / (Mo + W)) of the atomic percentage of Cr and the sum of atoms Mo and W, and the sum (Cr + Mo + W) of the atomic percentages of Cr, Mo and W can also be seen in table 1.
    The manufacturing method of this nickel-based superalloy for the 700C ultra supercritical coal power plants comprises the following steps:
    Select high-quality raw materials
    quality and put 0.06% weight in Ç, 24.7% weight in Cr, 12.9% weight from Co, 0. 53% weight in Mo, 2.23% weight in W, 1.59% weight from Nb, 1 .62 % weight of You, 1.54 % by weight in Al, 0.004% weight from B, 0, 005% weight in Zr, 0.15% weight in V, 54% weight of Ni and 5% in weight of materials dry auxiliaries
    with a purity of 99.5% for a vacuum induction furnace and auxiliary materials consisting of 40% by weight of
    CaF2, 40 wt% CaO and 20 wt% Al2O3. These raw materials are melted in the vacuum induction furnace under vacuum conditions of 10-3Bar. After the raw materials are completely melted, the molten metal is
    Petition 870150006884, of 12/14/2015, p. 36/58
    32/45 refined for 10 minutes to remove the gases, keeping the vacuum no lower than 10-3Bar. After refining is complete, load with Argon gas until the pressure reaches 0.4bar, adding 0.5% by weight of Ni20Ca alloy at the same time to remove the harmful impurity element S. When the temperature of the molten metal is at 1520 ° C before pouring; add 0.025% by weight of Ni-20Mg alloy and 0.005% by weight of La metal instead of performing desulfurization and purification. To fully melt the materials, mixing the molten metal well, filtering the molten metal and pouring the molten metal into the molds, the alloy ingot will form in an Argon atmosphere.
    Refuse the alloy ingot by refluxing the slag under a protective atmosphere. Remove the oxide layer from the surface of the welded alloy ingot with the electrode, perform slag remelting using the purified complex quinary slag system (40% CaF2 + 25% Al2O3 + 15% CaO + 10% MgO + 10% TiO2), in which the slag is extracted while SiO2 is guaranteed to be less than 0.5%. The electro slag ingot is cooked for 4 hours at a temperature of 800C, keeping the casting voltage at 250kg / h; and finally annealing the remelted ingot for 1 hour at a temperature of 900C;
    Carry out diffusion annealing in the remelted alloy ingot at a temperature of 1,190C and
    Petition 870150006884, of 12/14/2015, p. 37/58
    33/45 billet forging at a temperature of 1,200C, forging the alloy ingot in a 15mm bar product □ for three times reheating, implementing a solid solution treatment of the bar product for 1h at a temperature of 1,150C, cool the water and age the product in a bar for 16 hours at a temperature of 800C, cool the air. In this way, the weight fraction of the □□ reinforcement phase of this nickel-based super alloy for the 700C ultra supercritical coal power plants is 17.2% by weight.
    Comparative example 1:
    The nickel-based super alloy for the 700C ultra supercritical coal power plants comprises C, Cr, Co, Mo, W, Nb, Ti, Al, B, Zr, Mg, V, La, Ni and the impurity elements inevitable. The weight percentages actually tested for chemical composition and the weight percentages of the impurities S, P, Si and Mn can be seen in table 1. The (Al / (Ti + Nb)) index of the atomic percentage of Al for the sum of the atomic percentage of Ti and Nb, the sum of (Nb + Ti + Al) of the atomic percentages of Al, Ti and Nb, the index (Cr / (Mo + W)) of the atomic percentage of Cr and the sum of Mo atoms and W, and the sum (Cr + Mo + W) of the atomic percentages of Cr, Mo and W can also be seen in table 1.
    The manufacturing method of this
    Petition 870150006884, of 12/14/2015, p. 38/58
    34/45 nickel-based superalloy for 700% ultra supercritical coal power plants comprises the following steps:
    Select raw materials from high quality and put 0.05% weight in C, 24.98% weight in Cr, 14.6% weight in Co, 1.36% weight in Mo, 1.19% weight in W, 1.54% weight in Nb, 1.53% weight of You, 1.51% by weight in Al, 0.002% weight in B, 0.04% Zr weight, 53% Ni and weight 0.5 % in
    weight of dry auxiliary materials with a purity of 99.5% for a vacuum induction furnace and auxiliary materials consisting of 40% by weight of CaF2, 40% by weight of CaO and 20% by weight of Al2O3. These raw materials are melted in the vacuum induction furnace under vacuum conditions of 10-3Bar. After the raw materials are completely melted, load with Argon gas until the pressure reaches 0.4 bar, adding 0.5% by weight of Ni-20Ca alloy at the same time to remove the harmful impurity element S. When the temperature the molten metal is at 1520% before pouring; add
    0.015% by weight of Ni-20Mg alloy and 0.015% by weight of La metal instead of performing desulfurization and purification. To fully melt the materials, mixing the molten metal well, filtering the molten metal and pouring the molten metal into the molds, the alloy ingot will form in an Argon atmosphere.
    Refuse the alloy ingot by means of vacuum remelting.
    Petition 870150006884, of 12/14/2015, p. 39/58
    35/45
    Annealing the electrode for 1 hour at a temperature of 900C, removes the oxide layer from the surface; weld the electrode of the alloy ingots to a vacuum of 10-3mmHg; then, merge the two with a voltage of 25V; control the vacuum at 10-3mmHg; keep the melting index at 250kg / h; and finally annealing the ingot of the VAR alloy for 1 hour at a temperature of 900C; perform the annealing diffusion on the ingot of the VAR re-cast alloy at a temperature of 1,190C and forge the alloy ingot at 1200 C, in the □ 15mm bar product for three times the reheating, implementing the annealing of the solid solution in the product in bar for 1 hour at a temperature of 1150C, cool the water and age the product in bar for 16 hours at a temperature of 800C, cool the air. In this way, the weight fraction of the □□ reinforcement phase of this nickel-based superalloy for the 700C ultra supercritical coal power plants is 16% by weight.
    Carry out diffusion annealing in the remelted alloy ingot at a temperature of 1.190C and forging billet at a temperature of 1,200C, forging the alloy ingot in a 15mm bar product □ for three times the reheating, implement a solution treatment solid product bar for 1h at a temperature of 1.150C, cool the water and age the product bar for 16 hours at a temperature of
    Petition 870150006884, of 12/14/2015, p. 40/58
    36/45
    800C, cool the air. In this way, the weight fraction of the □□ reinforcement phase of this nickel-based super alloy for the 700C ultra supercritical coal power plants is 17.2% by weight.
    Comparative example 2:
    The nickel-based super alloy for the 700C ultra supercritical coal power plants comprises C, Cr, Co, Mo, W, Nb, Ti, Al, B, Zr, Mg, V, La, Ni and the impurity elements inevitable. The weight percentages actually tested for chemical composition and the weight percentages of the impurities S, P, Si and Mn can be seen in table 1. The (Al / (Ti + Nb)) index of the atomic percentage of Al for the sum of the atomic percentage of Ti and Nb, the sum of (Nb + Ti + Al) of the atomic percentages of Al, Ti and Nb, the index (Cr / (Mo + W)) of the atomic percentage of Cr and the sum of Mo atoms and W, and the sum (Cr + Mo + W) of the atomic percentages of Cr, Mo and W can also be seen in table 1.
    The manufacturing method of this nickel-based superalloy for the 7 00C ultra supercritical coal power plants comprises the following steps:
    Select raw materials from high quality and put 0.05% weight in C, 24.4% by weight in Cr, 13.6% weight in Co, 1.19% weight in Mo, 1.06% weight in W, 1.81% weight in Nb, 1.73% weight of You, 1.14% by weight in Al,
    Petition 870150006884, of 12/14/2015, p. 41/58
    37/45
    0.003% weight of B, 0.05% weight of Zr, 0.16% weight of V, 54% Ni and 0.5% by weight of dry auxiliary materials with a purity of 99.5% for an induction furnace vacuum and auxiliary materials consisting of 40 wt% CaF2, 40 wt% CaO and 20 wt% Al2O3. These raw materials are melted in the vacuum induction furnace under vacuum conditions of 10-3Bar. After refining is complete, load with Argon gas until the pressure reaches 0.4bar, adding 0.5% by weight of Ni20Ca alloy at the same time to remove the harmful impurity element S. When the temperature of the molten metal is at 1520 ° C before pouring; add 0.020% by weight of Ni-20Mg alloy and 0.005% by weight of La metal instead of performing desulfurization and purification. To fully melt the materials, mixing the molten metal well, filtering the molten metal and pouring the molten metal into the molds, the alloy ingot will form in an Argon atmosphere.
    Refuse the alloy ingot by means of vacuum remelting.
    Annealing the electrode for 1 hour at a temperature of 900C, removes the oxide layer from the surface; weld the electrode of the alloy ingots to a vacuum of 10-3mmHg; merge the two with a voltage of
    25V; control the vacuum at 10-3mmHg; keep the melting index at 250kg / h; and finally annealing the ingot of the VAR alloy for 1 hour at a temperature of 900C;
    Petition 870150006884, of 12/14/2015, p. 42/58
    38/45 perform the annealing diffusion on the ingot of the re-cast VAR alloy at a temperature of 1.190C and forge the alloy ingot at 1200C, in the Ü15mm bar product for three times the reheating, implementing the treatment of the solid solution in the product in bar for 1 hour at a temperature of 1150C, cool the water and age the product in bar for 16 hours at a temperature of 800C, cool the air. This way, the weight fraction of the □□ reinforcement phase of this nickel-based superalloy for the 700C ultra supercritical coal power plants is 13.4% by weight.
    Comparative example 3:
    The nickel-based super alloy for the 700C ultra supercritical coal power plants comprises C, Cr, Co, Mo, W, Nb, Ti, Al, B, Zr, Mg, V, La, Ni and the impurity elements inevitable. The weight percentages actually tested for chemical composition and the weight percentages of the impurities S, P, Si and Mn can be seen in table 1. The (Al / (Ti + Nb)) index of the atomic percentage of Al for the sum of the atomic percentage of Ti and Nb, the sum of (Nb + Ti + Al) of the atomic percentages of Al, Ti and Nb, the index (Cr / (Mo + W)) of the atomic percentage of Cr and the sum of Mo atoms and W, and the sum (Cr + Mo + W) of the atomic percentages of Cr, Mo and W can also be seen in table 1.
    Petition 870150006884, of 12/14/2015, p. 43/58
    39/45
    The manufacturing method of this nickel-based superalloy for 700% ultra supercritical coal power plants comprises the following steps:
    Select high quality raw materials and add 0.06% C, 24.4% Cr, 12.91% Co, 3.41% Mo, 2.33% W, 1.59 % weight of Nb, 1.63% weight of Ti, 1.53% weight of Al, 0.004% weight of B, 0.005% weight of Zr, 0.15% weight of V, 51% of Ni and 5% by weight of auxiliary materials dried with a purity of 99.5% for a vacuum induction furnace and auxiliary materials consisting of 40% by weight of CaF2, 40% by weight of CaO and 20% by weight of Al2O3. These raw materials are melted in the vacuum induction furnace under vacuum conditions of 10-3Bar.
    After the raw materials are completely melted, refine the molten metal for more than 10 min to remove the gases keeping the vacuum at 10-3Bar. After refining is complete, load with Argon gas until the pressure reaches 0.4 bar, adding 0.5% by weight of Ni-20Ca alloy at the same time to remove the harmful impurity element S. When the temperature of the molten metal is at 1520% before pouring; add 0.025% by weight of Ni-20Mg alloy and 0.005% by weight of La metal instead of performing desulfurization and purification. Fully melt the materials, mixing the molten metal well, filtering the molten metal and
    Petition 870150006884, of 12/14/2015, p. 44/58
    40/45 pouring the molten metal into the molds, the alloy ingot will form in an argon atmosphere.
    Refuse the alloy ingot by refluxing the slag under a protective atmosphere. Remove the oxide layer from the surface of the welded alloy ingot with the electrode. Perform slag remelting using the purified complex quinary slag system (40% CaF2 + 25% Al2O3 + 15% CaO + 10% MgO + 10% TiO2), where the slag is extracted while SiO2 is ensured to be less than 0.5% and the electro slag ingot is baked for 4 hours at a temperature of 800C, keeping the casting voltage at 50V and the casting rate at 250kg / h. Finally, anneal the remelted ingot for 1 hour at a temperature of 900C; perform the annealing diffusion on the ingot of the re-cast ESR alloy at a temperature of 1.190C and forge the ticket at a temperature of 1200C, forging the alloy ingot in the Ü15mm bar product for three times the reheating, implementing the treatment of the solid solution in the product in bar for 1 hour at a temperature of 1150C, cool the water and age the product in bar for 16 hours at a temperature of 800C, cool the air. In this way, the weight fraction of the □□ reinforcement phase of this nickel-based superalloy for the 700C ultra supercritical coal power plants is 18.2% by weight.
    Petition 870150006884, of 12/14/2015, p. 45/58
    41/45
    Table 1 - Chemical compositions of alloys in forms 1-6 and of alloy in comparative examples
    1-3
    ¥ 5 '| wSwfl OwwJg çCr-If 11 3-V 7 Li 5 X K- 35 tTLSfc-sõ4Λ1 Cr /Hfefll - | S | - a ™ · - C.C33 34.1C 14-CC C.33 1.C3 1.43 1 .4 « 1.33 0.005 C -Cl 0.005 C .13 0.005 0.0005 0.003 C-C3 C.C31,157 5,331 7.17 ZB.T15 3 L.L34 34. » 1C.Z3 1.34 1.C3 Z.K. 1.43 1.Í3 0.003 C .03 0.003 C .17 0.003 0.0004 0.003 C.C3 C.C31.ΖΕΣ E.177 25.50 7T.ET7 3 C.C « 34.45 14 _4l 3.41 1.14 1.33 1 ." l. « 0.007 C -C4 0.005 C-13 0.005 0.0005 0.003 C.C3 C.C3 3 * 1 1.1BD 5.B77 13.05 75,641 4 Ç." 34. » 14. « 3.34 1.13 l. « 1 .34 1.33 0.007 C -C4 0.005 C-13 0.005 0.0005 0.003 C.C3 C.C3 3 * 1 1.1B5 5.BE5 13.77 aa T 3 C.C4 34.14 13. « 3.Cl 1.13 1.43 1.43 1.43 0.005 C.C3 0.004 c.i-r 0.005 O.OOOB 0.004 c.c * C.C3 3L_ 1,173 5.BBS 17.54 75.T15 B C.C4 34. « 13.73 C.33 3.31 1.33 1 -35 1.43 0.004 C.C3 0.003 C-13 0.005 0.0005 0.003 C.C7 C.C3 3 * 1 1.1ZD 5.BZS 7B.E. TT.4TO ZJJíí.LiI: .J - C.C3 34.73 14. « 1.33 1.13 1.43 1 .47 1.43 O.OOZ C, C4 0.003 - - o.oozo 0.003 C.C3 C.C3 3tl i.i: < 5.T5E 73.77 73.43 E 3 ç." 34.14 13. « 1.13 1.C3 1.7 * 1 .w l.c-f 0.005 C.C3 0.004 c.i-r 0.005 O.OOOB 0.004 C.C5 C.C3 ^ »1 D. 750 3.5TB 73.T5 TT.31B 3- C.C4 34.13 13.73 3.33 3.31 1.33 1 .35 1.31 0.004 C.C3 0.003 C .13 0.003 0.0003 0.003 C.C7 C.C3 3L_ 1,141 E. 733 B.T1 1 B.3Z4
    The chemical compositions of the alloys in embodiments 1-6 are fully within the scope of the composition of the alloy of the present invention and within the requirements of the limiting conditions. The alloy in Comparative Example 1 is not added with V and La during casting. The Al / (Ti + Nb) atom number and the sum of the Nb + Ti + Al of the alloy in comparative example 2 do not comply with the alloy limiting conditions of the present invention. The atomic index Cr / (Mo + W) in comparative example 3 does not comply with the alloy limiting conditions of the present invention.
    Room temperature and high temperature traction tests:
    Nickel-based superalloys for 700 ° C ultra supercritical coal power plants in embodiments 1-6 and comparative examples 1-3
    Petition 870150006884, of 12/14/2015, p. 46/58
    42/45 are forged for round bars to perform tensile tests at room temperature and at 700 ° C and
    800 ° C, respectively. The results of the traction test can be seen in table 2.
    Table 2. Performance of traction at room temperature and high temperature of nickel-based alloys of the embodiments and comparative examples
    Test Temperature turns on Mechanical Property Production Force Rp0.2 / MPa Elastic Force Rm / MPa Elongation A /% Reduction of Area Z /% Room temperature Shapes 1 796.9 1225.8 32.4 38.9 2 824.7 1239.7 30.0 37.2 3 788.1 1214.9 28.0 33.0 4 814.2 1233.1 27.6 32.5 5 795.6 1218.3 24.2 32.36 804.1 1209.3 24.9 31.1 Comparative Examples 1 708.4 1119.5 18.1 22.3 2 652.9 1010.2 30.7 39.6 3 813.9 1219.4 23.5 32.1 700 ° C Shapes 1 646.0 1008.0 27.2 31.3 2 666.8 1023.0 24.8 32.4 3 645.3 986.0 27.2 31.4 4 662.1 1020.2 23.8 31.4 5 650.9 1006.9 23.9 30.56 645.2 1012.4 24.7 30.0 Comparative Examples 1 561.8 886.2 14.9 19.0 2 519.5 822.6 22.5 30.4 3 659.3 978.0 20.2 26.1 800 ° C Shapes 1 611.2 841.3 19.8 25.5 2 628.3 849.1 20.8 27.5 3 602.1 809.3 18.0 25.6 4 622.9 845.0 18.0 25.6 5 619.5 815.6 20.1 28.26 615.2 816.8 19.1 27.2 Comparative Examples 1 540.3 708.9 9.8 14.4 2 491.7 642.2 16.3 24.0 3 616.1 837.5 14.9 24.1
    From the data in table 2, you can
    Petition 870150006884, of 12/14/2015, p. 47/58
    43/45 be seen that the tensile test at room temperature shows that the elastic limit of nickel-based alloys of the embodiments and comparative examples is greater than 780MPa, the tensile strength is greater than 1,200MPa, the elongation is greater than 24.0%, and the reduction in area is greater than 32.0%. In the case of a 700C tensile test, the yield strength is greater than 640MPa, the tensile strength is greater than 980Mpa, the elongation is greater than 23.0%, and the reduction in area is greater than 30.0%. In the case of an 800C tensile test, the yield strength is greater than 600MPa, the tensile strength is greater than 800Mpa, the elongation is greater than 17.0%, the reduction in area is greater than 25.0%; the alloys have high tensile strength and tensile ductility at both ambient and elevated temperatures.
    Comparatively, for the alloy of comparative example 1 without V and La, not only does the tensile strength decrease, but it also reduces the tensile ductility by 35% ~ 50% compared to the embodiment, in particular, for the alloy with high S content. The alloy of the compositions Nb, Ti and Al in comparative example 2 do not comply with the restriction conditions, shows relatively low strength and reduced tensile strength by 15% ~ 20% compared to the embodiment , in addition to the equilibrium phase, this alloy contains phase η, as shown in figure 3. The alloy of the compositions Cr, Mo and W in comparative example 3, is not in
    Petition 870150006884, of 12/14/2015, p. 48/58
    44/45 compliance with the restriction conditions, shows that the strength and toughness are affected, and, in addition, there is a fragile σ phase that is detrimental to the equilibrium phase of the alloy, as shown in Figure 4. These results indicate that the scopes and conditions of restriction of the chemical composition limited by the present invention are strong guarantees for good tensile properties of the alloy.
    High temperature burst resistance tests:
    The nickel-based super alloys for the 700 ° C ultra supercritical coal power plants in embodiments 1-6 are forged in a bar product for breaking strength tests at 750C, 800C and 850C, respectively.
    In the condition of 750C / 205MPa, the resistance to rupture of the alloy in embodiments 1-6 is greater than 5,000h, the elongation is greater than 12.0%, the reduction in area is greater than 16.0%; in the condition of 800C / 125MPa the break resistance time is greater than 5,000h, the elongation is greater than 14.0%, the reduction in area is greater than 18.0%; in the condition of 850C / 100 MPa, the time of resistance to rupture is superior to 1,500h, the elongation is superior to 20,0%, and the reduction of area is superior to 25,0%.
    At 750C / 205MPa condition, the time
    Petition 870150006884, of 12/14/2015, p. 49/58
    45/45 alloy tensile strength in comparative examples 1-3 is less than 3,000h, elongation is less than 8.0%, the reduction in area is less than 11.0%; at 800 ° C / 125MPa the break resistance time is less than 2,500h, the elongation is less than 10.0%, the area reduction is less than 14.0%; at 850C / 100 MPa, the break resistance time is less than 750H, the elongation is less than 12.0%, and the area reduction is less than 17.0%.
    The nickel-based alloy of the present invention features with high forge, can be used to manufacture the highest temperature parts of the turbines and boilers of the 700C ultra supercritical coal power plants and can also be applied to other fields where it needs a material with high oxidation resistance, corrosion resistance, and high tensile strength and also creep resistance.
    权利要求:
    Claims (8)
    [1]
    1. NICKEL-BASED SUPER ALLOY FOR
    ULTRA SUPERCRITICAL BURNED COAL ENERGY PLANT
    700 ° C, consisting of: C 0.01 ~ 0.07% weight, Cr 23 ~ 25.5% weight, Co 10 ~ 14.6% weight, Mo 0.3 ~ 3.5% weight, W 0.5 ~ 2.5% weight, Nb 0.8 ~ 2.2% weight, Ti 1.0 ~ 2.5% weight, Al 1.0 ~ 2.5% weight, B 0.001% ~ 0.005 weight, Zr 0.01 ~ 0.3% in weight, Mg 0.002 ~ 0.015% weight, V 0.01 ~ 0.5% weight, La 0.001 ~ 0.005% weight, the Ni balance and elements of unavoidable impurities, including S <0.010% weight, P <0.015% weight, Si <0.3% by weight and Mn <0.5% by weight, where the index of the atomic percentage of Al to the sum of the atomic percentage of Ti and Nb is in the range of 1.0-1.3; the sum of the atomic percentages of Al, Ti and Nb is 5.5-6.2in%; the atomic percentage index of Cr for the sum of the atomic percentage of Mo and W is greater than 12, and the sum of the atomic percentages of Cr, Mo and W is not greater than 30%.
    [2]
    2/4
    0.01 ~ 0.3% by weight of Zr, 0.01 ~ 0.5% by weight of V, 48-58% by weight of Ni and 3-6% by weight of dry auxiliary materials with a purity greater than 99 , 5% for the vacuum induction furnace and auxiliary materials consisting of 40% by weight of CaF2, 40% by weight of CaO and 20% by weight of Al2O3; melting these raw materials in the vacuum induction furnace to a vacuum condition of not less than 10-3Bar; after the raw materials are completely melted, refine the molten metal for more than 30 min to remove the gases keeping the vacuum at 10-3Bar; after refining is complete, charge with Argon gas until the pressure reaches 0.4bar, adding 0.3-0.6% weight of Ni-Ca alloy at the same time to remove the harmful impurity element S, where the temperature of the molten alloy is not less than 1,500%; add 0.01 ~ 0.025% weight of Ni-Mg alloy and 0 ~ 0.005% weight of metal La instead of performing desulfurization and purification; fully melt the materials, mixing the molten metal well, filtering the molten metal and moistening the molten metal into the mold; the alloy ingot will form an Argon atmosphere.
    - Step 2: perform diffusion annealing, forging, solid solution and treatment of the aging of the alloy to obtain the nickel-based superalloy for 700% ultra supercritical coal power plants.
    2. METHOD OF MANUFACTURING THE NICKEL-BASED SUPERLINK FOR ULTRA SUPERCRITICAL BURNED COAL ENERGY PLANT OF 700 o C, according to claim 1, characterized by comprising the following steps:
    - Step 1: Put 0.01 ~ 0.07% weight of
    C, 23 ~ 25.5% Cr weight, 10 ~ 14.6% Co weight, 0.3 ~ 3.5% Mo weight, 0.5 ~ 2.5% W weight, 0.8 ~ 2.2% Nb weight, 1.0 ~ 2.5% Ti weight, 1.0 ~ 2.5% Al weight, 0.001 ~ 0.005% B weight,
    Petition 870190085461, of 08/30/2019, p. 10/13
    [3]
    3/4
    NICKEL-BASED FOR 700 ° C ULTRA SUPERCRITICAL BURNED COAL ENERGY PLANT, according to claim 2, characterized in that, in step 2, the diffusion annealing temperature is implemented at 1,150 ~ 1,220 ° C, and the duration is 16 ~ 48 h.
    3. “SUPERLIGA MANUFACTURING METHOD
    Petition 870190085461, of 08/30/2019, p. 11/13
    [4]
    4/4 before diffusion annealing, the alloy ingot is refined again by vacuum arc remelting or by electro-slag remelting in a shielding gas atmosphere.
    8. “METHOD OF MANUFACTURING THE NICKEL-BASED SUPERLINK FOR ULTRA SUPERCRITICAL BURNED COAL ENERGY PLANT 700 ° C”, according to claim 7, characterized by the fact that, if the recirculating vacuum arc method is adopted in step 2, the re-melting index should be strictly controlled at less than 300kg / h.
    9. “METHOD OF MANUFACTURING THE NICKEL-BASED SUPERLINK FOR A SUPERCRITICAL SUPERCRITICAL BURNED COAL POWER PLANT OF 700 ° C”, according to claim 7, characterized by the fact that, when the remelting of electro-slag in a gas atmosphere protection system is adopted in step 2, a purified complex quinary slag system is used; the purified complex quinary slag system comprises 40 ~ 45 wt% CaF2, 20 ~ 30 wt% Al2O3, 15 ~ 20 wt% CaO, 5 ~ 10 wt% MgO and 5-10 wt% TiO2 ; prior to use, the purified complex quinary slag system must be extracted to ensure SiO2 <0.5%, and must be cooked for 4 hours at a temperature of
    4. “SUPERLIGA MANUFACTURING METHOD
    NICKEL BASED FOR BURNED COAL POWER PLANT
    ULTRA SUPERCRITICAL 700 ° C ”, according to claim 2, characterized by the fact that, in step 2, the billet forging temperature is not less than 1.050C.
    [5]
    5. “SUPERLIGA MANUFACTURING METHOD
    NICKEL BASED FOR ULTRA SUPERCRITICAL BURNED COAL ENERGY PLANT 700 ° C ”, according to claim 2, characterized in that, in step 2, the treatment temperature of the solid solution is implemented at 1,100 ~ 1,200C, and the duration is 0.5 ~ 2h.
    [6]
    6. “SUPERLIGA MANUFACTURING METHOD
    NICKEL BASED FOR BURNED COAL POWER PLANT
    ULTRA SUPERCRITICAL 700 ° C ”, according to claim 2, characterized by the fact that, in step2, the treatment temperature of the solid solution is implemented at 800C and the duration is 4 ~ 16h.
    [7]
    7. “METHOD OF MANUFACTURING THE NICKEL-BASED SUPERLINK FOR ULTRA SUPERCRITICAL BURNED COAL ENERGY PLANT 700 ° C”, according to claim 2, characterized by the fact that, in step2,
    Petition 870190085461, of 08/30/2019, p. 12/13
    [8]
    8 00 C.
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    同族专利:
    公开号 | 公开日
    KR20160013864A|2016-02-05|
    CN103898371B|2016-04-06|
    EP3109331A4|2017-10-11|
    BR112015031328A2|2017-07-25|
    KR101764755B1|2017-08-03|
    CN103898371A|2014-07-02|
    EP3109331A1|2016-12-28|
    EP3109331B1|2019-01-30|
    WO2015123918A1|2015-08-27|
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    法律状态:
    2017-08-08| B08F| Application fees: dismissal - article 86 of industrial property law|
    2017-11-14| B08G| Application fees: restoration|
    2019-06-11| B06A| Notification to applicant to reply to the report for non-patentability or inadequacy of the application according art. 36 industrial patent law|
    2019-12-10| B09A| Decision: intention to grant|
    2020-01-28| B16A| Patent or certificate of addition of invention granted|Free format text: PRAZO DE VALIDADE: 20 (VINTE) ANOS CONTADOS A PARTIR DE 16/04/2014, OBSERVADAS AS CONDICOES LEGAIS. |
    优先权:
    申请号 | 申请日 | 专利标题
    CN201410054132.2A|CN103898371B|2014-02-18|2014-02-18|700 DEG C of grade ultra supercritical coal power station nickel base superalloys and preparation thereof|
    PCT/CN2014/075474|WO2015123918A1|2014-02-18|2014-04-16|High-temperature nickel-based alloy for 700°c grade ultra-supercritical coal-fired power station and preparation thereof|
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