Patent Application
20110070088
The present invention generally relates to turbine rotors, including those used in steam turbines. More particularly, this invention relates to an alloy suitable for use in high pressure and intermediate pressure stages of a steam turbine rotor and capable of increasing high temperature properties of such a rotor.
Rotors used in steam turbines, gas turbines, gas turbine engines and jet engines experience a range of operating conditions along their axial lengths. The different operating conditions complicate the selection of a suitable rotor material and the manufacturing of the rotor because a material optimized to satisfy one operating condition may not be optimal for meeting another operating condition. For instance, the inlet and exhaust areas of a steam turbine rotor have different material property requirements. High temperature and high pressure conditions within a high pressure (HP) stage at the inlet of a steam turbine typically require a material with high creep rupture strength, though only relatively moderate toughness. On the other hand, a low pressure (LP) stage at the exhaust of a steam turbine does not demand the same level of high temperature creep strength, but suitable materials typically must exhibit very high toughness because of the high loads imposed by long turbine blades used in the exhaust area.
Because a monolithic (monoblock) rotor (i.e., a rotor that is not an assembly) of a single chemistry cannot meet the property requirements of each of the LP, IP and HP stages for the reasons discussed above, rotors constructed by assembling segments of different chemistries are widely used. For example, large steam turbines typically have a bolted construction made up of separate rotor segments contained in separate shells or hoods for use in different sections of the turbine. The steam turbine industry currently favors CrMoV low alloy steels (typically, by weight, about 1% chromium, 1% molybdenum, 0.25% vanadium, up to 0.3% carbon, the balance iron and possibly lesser additions of silicon, manganese, etc. for use in the HP stage and NiCrMoV low alloy steels for use in the LP stage. NiMoV low alloy steels have also been widely used as materials for the various stages. A particular example of a CrMoV alloy contains, by weight, 1.0 to 1.5% chromium, 1.0 to 1.5% molybdenum, 0.2 to 0.3% vanadium, 0.25 to 0.35% carbon, 0.25 to 1.00% manganese, 0.2 to 0.75% nickel, up to 0.30% silicon, the balance iron and incidental impurities, for example, up to 0.010% phosphorous, up to 0.010% sulfur, up to 0.010% tin, up to 0.020% arsenic, and up to 0.015% aluminum.
While rotors fabricated from CrMoV low alloy steel compositions are widely used, the current maximum design temperature for CrMoV steels is about 1050° F. (about 565° C.). As higher inlet temperatures are sought, for example up to about 1065° F. (about 575° C.), to increase steam turbine efficiencies, chromium steel alloys (typically about 9 to 14 weight percent chromium) with varying levels of Mo, V, W, Nb, B must typically be used to meet the higher temperature conditions in the HP stage of the steam turbine. While capable of operating at temperatures exceeding 565° C. within the HP stage of a steam turbine, rotor forgings produced from these alloys incur higher costs and additional measures are often required to address thermal expansion mismatches with alloys used in the cooler stages of the rotor.
Modifications to CrMoV low alloy steels have been made to achieve desired properties for various other applications. For example, CrMoV bolting steels used in steam turbine applications may include additions of aluminum, boron and/or titanium to improve high temperature strength and ductility. Examples include alloys designated as 7 CrMoVTiB 10-10 and 20 CrMoVTiB 4-10. One such bolt alloy composition has been reported to contain, by weight, 0.9 to 1.2% chromium, 0.9 to 1.1% molybdenum, 0.6 to 0.8% vanadium, 0.35 to 0.75% manganese, 0.17 to 0.23% carbon, 0.07 to 0.15% titanium, 0.015 to 0.080% aluminum, 0.001 to 0.010% boron, up to 0.20% nickel, up to 0.40% silicon, up to 0.020% phosphorous, up to 0.020% sulfur, up to 0.020% tin, up to 0.020% arsenic, the balance iron. A particular commercial example is available from Corus Engineering Steels under the name Durehete 1055, and has been reported to contain, by weight, 1% chromium, 1% molybdenum, 0.7% vanadium, 0.5% manganese, 0.25% silicon, 0.2% carbon, 0.1% titanium, 0.04% aluminum, 0.003% boron, the balance iron. Boron has been reported to stabilize V4C3 carbides that serve as a strengthening phase in bolts formed of CrMoV alloys, and titanium has been reported to remove nitrogen from solution to prevent the formation of boron nitride precipitates. However, it is believed that boron has found limited use and titanium has not been used as additives to CrMoV alloys from which rotors are forged. Furthermore, forged steam turbine rotors have vastly different property requirements relative to bolts used in steam turbine applications, for example, to hold two rotor sections together or to hold the two shell halves together for steam containment.
The present invention provides an alloy suitable for use in a rotor, for example, one or more regions of a steam turbine rotor, as well as a forged rotor formed with the alloy. In particular, the present invention involves modifications to a CrMoV low alloy steel to promote high temperature properties that enable a rotor formed therefrom to exhibit improved properties, for example, creep resistance, for use in the high pressure stage of a steam turbine.
According to one aspect of the invention, the alloy, consists of (by weight) 0.20 to 0.30% carbon, 0.80 to 1.5% chromium, 0.80 to 1.5% molybdenum, 0.50 to 0.90% vanadium, 0.30 to 0.80% nickel, 0.05 to 0.15% titanium, 0.20 to 1.0 manganese, and 0.005 to 0.012% born, the balance iron, optionally low levels of other alloying constituents, and incidental impurities. The alloy may be applied to the steam turbine applications such as high pressure (HP) rotors that require a monoblock forging, intermediate pressure (IP) rotors that require a monoblock forging, and combination HP-IP Rotors that require a monoblock forging. The alloy is also suitable for use as a HP or IP rotor section attached (for example, bolted or welded) to a low pressure (LP) rotor section formed of a different alloy composition.
Another aspect of the invention is a turbine rotor having at least a portion forged from the alloy described above. Though the chemistry of the alloy is similar to CrMoV bolting alloys containing titanium and boron, the latter were developed for bolting applications where smaller diameter bar stock is required bolting alloys, whereas the chemistry and heat treatment of the present alloy are modified for the production of large diameter forgings capable of addressing HP and IP rotor application requirements.
A significant advantage of this invention is that the alloy is capable of exhibiting increased creep strength and improved microstructure stability at temperatures above 1050° F. (about 565° C.), for example up to about 1065° F. (about 575° C.), relative to conventional CrMoV alloys. As a result, higher HP inlet temperatures are possible that can achieve enhanced steam turbine performance and efficiencies without having to resort to significantly higher costs associated with alloys such as 9-12% chromium heat resistant alloys. Furthermore, by avoiding the use of 9-12% chromium alloys and other alloys having coefficients of thermal expansion different from conventional CrMoV alloy steels, forgings produced from the alloy of this invention can be utilized in the service market as part of a retrofit package for performance enhancement of existing steam turbine units, as well as in new steam turbine designs.
Other aspects and advantages of this invention will be better appreciated from the following detailed description.
The present invention pertains to an alloy suitable for use in a steam turbine applications, such as a monoblock (one-piece) rotor forging 10 of the type represented in
Alternatively, it is foreseeable that the alloy could be utilized to produce a HP or IP rotor forging section, which may be either bolted or welded to a LP rotor forging section or another HP rotor forging section of another material to produce a combination steam turbine rotor assembly 20 of the type represented in
To achieve mechanical properties necessary for the monoblock rotor forging 10 of
The alloy is believed to provide advantages when used in a forged rotor, and particularly the HP region and optionally the IP region of a steam turbine rotor. For example, the inclusion of both boron and titanium is believed to promote microstructure stabilization at temperatures above 1050° F. (about 565° C.), for example up to about 1065° F. (about 575° C.) and possibly higher, providing an increase in creep strength relative to conventional CrMoV alloys. Though appearing to be a rather minor increase of up to about 15° F. (about 10° C.), such an increase in HP inlet design temperature would be able to achieve enhanced steam turbine performance and efficiencies without having to resort to significantly higher costs associated with other alloys, such as 9-12% chromium heat resistant alloys. Furthermore, by avoiding the use of 9-12% chromium alloys and other alloys whose coefficients of thermal expansion are different from conventional CrMoV alloy steels, forgings produced from the alloy of this invention can be utilized in the service market as part of a retrofit package for performance enhancement of existing steam turbine units, as well as in new steam turbine designs.
The alloy described above is based on a nominal 1% CrMoVTiB alloy previously applied only to steam bolting applications. Relative to steam bolting applications, rotor forging applications require the production of forgings with significantly greater diameters. For example, HP and IP rotor forgings are typically manufactured with a maximum diameter for the final forging in the range of about twenty to about forty-eight inches (about 50 to about 120 cm). Consequently, the nominal 1% CrMoVTiB chemistry for bolting applications was necessarily tailored for the production of larger diameter rotor forgings. For example, the target manganese level was increased to improve the hardenability of the alloy, the target nickel level was increased to improve the hardenability and fracture toughness of the alloy, and the target aluminum level was decreased to avoid the formation oxides that would be retained in the final product.
As previously noted, the alloy of this invention is adapted to be cast and forged to form a monoblock (one-piece) HP or IP rotor forging 10 of the type shown in
If the alloy of this invention is used to form multiple regions of the rotor forging 10, for example, in accordance with the aforementioned U.S. patents to Schwant et al. and Ganesh et al., different heat treatment temperatures and durations may be used if deemed desirable or necessary. For example, a furnace with multiple temperature zones may be used to provide an appropriate heat treatment temperature for regions of the rotor forging corresponding to the different regions of the rotor forging 10. As understood in the art, such differential heat treatments may include different temperatures for solution, austenitizing, aging and/or tempering treatments that may be performed on the rotor forging. For example, a higher temperature austenitizing treatment may be used if higher creep rupture strength is desired for the HP region, while relatively lower temperatures may be used if higher toughness is needed for the IP or LP regions. Differential cooling after austenitizing may also be used. For example, relatively slow cooling may be used to achieve beneficial precipitation reactions, reduce thermal stresses, and/or enhance creep rupture strength in the HP region, whereas more rapid cooling may be used to achieve full section hardening, avoid harmful precipitation reactions, and/or enhance toughness for the IP or LP regions. Optimal temperatures, durations, and heating and cooling rates will generally be within the capability of one skilled in the art.
While the invention has been described in terms of particular embodiments, it is apparent that other forms could be adopted by one skilled in the art. Therefore, the scope of the invention is to be limited only by the following claims.
