US20060266439A1 - Heat and corrosion resistant cast austenitic stainless steel alloy with improved high temperature strength - Google Patents
Heat and corrosion resistant cast austenitic stainless steel alloy with improved high temperature strength Download PDFInfo
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- US20060266439A1 US20060266439A1 US11/495,671 US49567106A US2006266439A1 US 20060266439 A1 US20060266439 A1 US 20060266439A1 US 49567106 A US49567106 A US 49567106A US 2006266439 A1 US2006266439 A1 US 2006266439A1
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
Definitions
- This disclosure relates generally to cast austenitic stainless steel alloys of the CF8C type with improved high temperature strength. More particularly, this disclosure relates to CF8C type stainless steel alloys and articles cast therefrom having excellent high temperature creep strength, and aging resistance, and which exhibit a stable austenitic microstructure with substantially no delta ferrite after casting and high temperature aging.
- any new material should have good casting characteristics like melt fluidity, hot tear resistance, and weldability.
- a significant factor in the cost of producing a casting is the post casting stress relief or solution heat treatment typically required for stainless steel castings. Eliminating the need for post casting heat treatments can result in substantial time and money savings for casting manufacturers. These cost savings can be even higher for large components like steam turbine casings where large furnaces have to be used. Therefore, any new material should have the desired properties in the as-cast state, that is, without the need for post casting heat treatment.
- CF8C is a commercially available cast austenitic stainless steel that is relatively inexpensive. However, standard practice is to solution treat CF8C castings at 1050° C., which like discussed above, may increase its cost for some applications.
- Currently-available cast austenitic stainless CF8C steels may include from 18 wt. % to 21 wt. % chromium, 9 wt. % to 12 wt. % nickel and smaller amounts of carbon, silicon, manganese, phosphorous, sulfur and niobium.
- CF8C typically includes about 2 wt. % silicon, about 1.5 wt. % manganese and about 0.04 wt. % sulfur.
- CF8C is a niobium stabilized grade of austenitic stainless steel most suitable for applications at temperatures below 500° C. In the standard form CF8C has poor strength at temperatures above 600° C. It also does not provide adequate cyclic oxidation resistance at temperatures exceeding 700° C., does not provide sufficient ductility, does not have the requisite long-term stability of the original microstructure after high temperature aging, and lacks long-term resistance to cracking during severe thermal cycling.
- delta ferrite is present in the as-cast microstructure.
- This delta-ferrite in the microstructure transforms to sigma ( ⁇ ) phase during prolonged high-temperature exposure, decreasing the ductility of the material, particularly at lower or ambient temperatures.
- ⁇ sigma
- the absence of delta ferrite and sigma phase in the microstructure in the as-cast state and after prolonged exposure to high temperatures (high temperature aging) is an important advantage to preserve the as-cast properties of the material during the lifetime of a component created with the material.
- a class of stainless steel alloys is described in U.S. Pat. No. 5,340,534 issued to Magee (hereinafter, “the '534 patent”.)
- the '534 patent seeks to improve the galling resistance and corrosion resistance of stainless steel alloys.
- a concentration of silicon above 2.25% is an important contributor to the improved galling resistance of the alloy.
- Silicon is also important for metal fluidity of casting steels. However, silicon promotes the formation of ferrite, sigma phases and niobium rich lanes or other silicide phases in the steel, and ferrite volume measurements indicate ferrite volumes between 2.3 and 7 percent in different heats of alloys described in the '534 patent.
- a modified CF8C type steel alloy which has good casting characteristics, improved strength and creep properties at temperatures above 600° C. in the as-cast state, and which exhibits a stable and completely austenitic microstructure after casting and high temperature aging, so that the improved strength and ductility of the material is maintained over the lifetime of the alloy.
- Completely austenitic microstructure refers to a nearly 100% austenitic microstructure which is substantially free of delta ferrite and sigma phases of steel.
- the disclosed system is directed to overcoming one or more of the problems set forth above.
- the present disclosure is directed to a heat and corrosion resistant cast austenitic stainless steel alloy which contains less than about 15% nickel.
- the alloy has a completely austenitic microstructure in an as-cast state, and a creep rupture life exceeding 20,000 hrs at a stress of 35 MPa and a temperature of 850° C., when creep tested in the as-cast state under ASTM E139 test conditions.
- the present disclosure is directed to a heat and corrosion resistant cast austenitic stainless steel alloy containing less than 15% nickel.
- the alloy has a creep rupture life exceeding 3,000 hrs and a minimum creep rate of less than 1 ⁇ 10 ⁇ 3 at a stress of 100 MPa and a temperature of 750° C., when creep tested in the as-cast state under ASTM E139 test conditions.
- the alloy also has a 0.2% yield strength exceeding 130 MPa at 750° C. in the as-cast state, and a decrease in 0.2% yield strength from 750 to 900° C. of less than 20%; and, a completely austenitic microstructure after casting.
- the present disclosure is directed to an article made of a heat and corrosion resistant cast austenitic stainless steel alloy which contains less than about 15% nickel and has a completely austenitic microstructure.
- the article also shows no detectable ferromagnetic phases like ferrite or martensite when measured with a measurement device after casting and after high temperature aging for 3000 hrs at 750° C.
- the article has a creep rupture life exceeding 20,000 hrs at a stress of 35 MPa and a temperature of 850° C., when creep tested in the as-cast state under ASTM El 39 test conditions and a creep rupture life exceeding 2000 hours and a minimum creep rate less than 5 ⁇ 10 ⁇ 3 at a stress of 100 MPa and a temperature of 750° C., when creep tested in the as-cast state under ASTM E139 test conditions.
- the present disclosure also discloses a heat and corrosion resistant cast austenitic stainless steel alloy which has a completely austenitic microstructure in the as-cast state.
- the alloy includes about 0.05 weight percent to about 0.15 weight percent of carbon, about 1.5 weight percent to about 3.5 weight percent copper, about 0.25 weight percent to about 1.0 weight percent tungsten, and about 0.6 weight percent to about 1.5 weight percent of niobium.
- FIG. 1 a is an SEM micrograph of the microstructure of an exemplary polished and etched as-cast CF8C alloy.
- FIG. 1 b is an SEM micrograph of the microstructure of an exemplary polished and etched as-cast CF8C-Plus alloy.
- FIG. 2 a shows the microstructure of an exemplary CF8C alloy before high temperature aging.
- FIG. 2 b shows the microstructure of an exemplary CF8C alloy after high temperature aging.
- FIG. 3 a shows the microstructure of an exemplary CF8C-Plus alloy before high temperature aging.
- FIG. 3 b shows the microstructure of an exemplary CF8C-Plus alloy after high temperature aging.
- FIG. 4 a is a TEM image of the microstructure of an exemplary CF8C alloy after creep testing at 850° C. and 35 MPa.
- FIG. 4 b is a TEM image of the microstructure of an exemplary CF8C-Plus alloy after creep testing at 850° C. and 35 MPa.
- CF8C is the traditional cast equivalent of type 347 stainless steel.
- the chemistry of CF8C-Plus is based on the composition of CF8C with precise additions of nickel (Ni), manganese (Mn), and nitrogen (N) combined with a reduction in silicon (Si) and adjustments of other minor alloying elements. These alloy modifications were made to improve the high-temperature mechanical properties and the casting characteristics of the CF8C steel using inexpensive alloying elements without the need for post casting heat treatments.
- Table I is directed towards the maximum and minimum ranges of the compositional elements made in accordance with the present disclosure.
- Table I also includes (in column labeled “Example alloy”) an example of an embodiment of an alloy made in accordance with the present disclosure.
- Embodiments covered by the present disclosure include alloys with any subset of compositional ranges falling within the minimum and maximum ranges shown in Table I.
- allowable ranges of cobalt (Co), vanadium (V), and titanium (Ti) may not significantly alter the performance of the resulting material.
- Co may range from 0 to about 5 weight percent
- V may range from 0 to about 3 weight percent
- Ti may range from 0 to about 0.2 weight percent without significantly altering the performance of the alloys.
- FIG. 1 a shows the microstructure of an exemplary polished and etched as-cast CF8C alloy
- FIG. 1 b shows the microstructure of an exemplary polished and etched as-cast CF8C-Plus alloy
- the microstructure of the as-cast CF8C alloy includes an austenite matrix with delta ferrite 10 pools in the interdentrite core regions, and niobium carbide (NbC) 12 in the interdentritic regions.
- the microstructure of the as-cast CF8C-Plus alloy does not show any delta ferrite 10 .
- the microstructure of CF8C-Plus alloy is fully austenitic with a mixture of chromium carbide (Cr 23 C 6 ) and NbC 12 in the interdentritic regions.
- a digital Fisher® Feritscope® was used to measure the ferrite content of both the CF8C and CF8C-Plus steel castings.
- the CF8C had a ferrite number of about 16.8+/ ⁇ 1.1, which is equivalent to about 14% delta ferrite, and the CF8C-Plus did not register any detectable ferromagnetic behavior, meaning it has less than about 0.1% delta ferrite. Both these macroscopic measurements and microscopic studies indicate that the CF8C-Plus material in the as-cast state is substantially free of delta ferrite 10 in the as-cast state.
- sand cast keel bars were encapsulated in quartz tubes, evacuated, and backfilled with argon. These were aged in an air box furnace at 750° C. for 3,000 hours. These specimens were polished and etched for optical microscopy using an etchant composed of glycerin, hydrochloric acid, nitric acid, and acetic acid having a volumetric ratio of 3:3:1:1. Scanning Electron Microscopy (SEM) analysis was performed on polished and unetched specimens using backscatter electron (BSE) imaging, and x-ray energy dispersive spectroscopy (XEDS) was performed on areas of interest.
- SEM Scanning Electron Microscopy
- BSE backscatter electron
- XEDS x-ray energy dispersive spectroscopy
- FIG. 2 a shows a BSE image of the microstructure of an exemplary CFSC alloy before high temperature aging
- FIG. 2 b shows a BSE image of the microstructure of an exemplary CF8C alloy after high temperature aging at 750° C. for 3,000 hours.
- Comparison of FIGS. 2 a and 2 b indicate a change in BSE image contrast in delta ferrite 10 of the aged material. XEDS analysis of these regions in the aged material indicates that they are enriched in silicon (Si) and chromium (Cr) compared to the delta-ferrite 10 found in the as-cast structure.
- Comparison of FIGS. 2 a and 2 b indicates that delta-ferrite 10 has transformed into sigma phase 14 after high temperature aging.
- FIG. 3 a shows a BSE image of the microstructure of an exemplary CF8C-Plus alloy before high temperature aging
- FIG. 3 b shows a BSE image of the microstructure of an exemplary CF8C-Plus alloy after high temperature aging at 750° C. for 3,000 hours.
- the CF8C-Plus steel alloys in FIG. 3 a and FIG. 3 b do not show the formation of any delta ferrite 10 or sigma phases 14 after high temperature aging.
- the structure of CF8C-Plus alloy before and after high temperature aging samples is austenitic with interdendritic carbides 16 .
- Table II compares the average tensile properties, namely 0.2% offset yield strength (YS), ultimate tensile strength (UTS), and ductility as measured as the percentage elongation at fracture (Elong.), and percentage reduction of cross sectional area at fracture (RA), for CF8C, and CF8C-Plus (CF8C+) steels as a function of temperature.
- the average yield strength of CF8C-Plus changes very little above 700° C., while that of CF8C steel shows significant weakening.
- the average ultimate tensile strength of the CF8C-Plus steel is higher for the entire temperature range compared to CF8C. This increase is significantly higher (>70 Mpa) at temperatures above 700° C.
- Table III compares the average creep rupture life of CF8C and CF8C-Plus (CF8C+) alloys at different stresses and temperatures. As seen in the table, the creep rupture life of CF8C-Plus steel is over an order of magnitude higher than that of CF8C steel in all cases.
- the creep ductility of CF8C-Plus steel both as measured as a percentage change in elongation and percentage change in area, also shows a significant improvement over that of CF8C steel. In most cases, this improvement in ductility over CF8C steel is over 100%.
- the minimum creep rate of CF8C-Plus steel also shows a significant decrease over that of CF8C. In most cases, this decrease in minimum creep rate is over an order of magnitude lower than that of CF8C.
- FIG. 4 a is a TEM image of the microstructure of CF8C after 493 hours of creep testing at 850° C. and 35 MPa.
- FIG. 4 b is the TEM image of the microstructure of CF8C-Plus after over 20,000 hours of creep testing at 850° C. and 35 MPa.
- Comparison of FIGS. 4 a and 4 b shows that the NbC 12 precipitates in the CF8C-Plus steel were less than about 50 nanometers in average diameter (as shown in FIG. 4 b ,) while the average diameter of these precipitates was over about 250 nanometers, with much larger spacing after only 493 hours of testing, in CF8C alloys (as shown in FIG. 4 a .)
- This alloy is used as the baseline to compare the effect of additional alloying elements in the alloy.
- the columns titled ‘CF8C+B’, ‘CF8C+W’, ‘CF8C+Cu’, and ‘CF8C+Al’ list the composition of the alloys obtained by adding about 0.005 weight percent of boron, about 0.45 weight percent of tungsten, about 2.5 weight percent of copper, and about 1.3 weight percent of aluminum, respectively, to the composition of the CF8C-Plus alloy.
- Table VII compares the tensile test and creep test results of the four alloy additions to the CF8C material. As the results indicate, samples with Al and B additions exhibited worse creep life than CF8C-Plus material, and were not, therefore, chosen for creep testing at 750° C. and 140 MPa. The results indicate that the alloys with the Cu and W additions performed better than the base CF8C-Plus material in high temperature creep. TABLE VII Tensile tests (ASTM E8 &E12) Creep strength (ASTM E139) YS (Mpa) UTS (Mpa) Creep Rupture life (hrs) Alloy 25 C. 850 C. 25 C. 850 C.
- both Cu and W together were added to the CF8C-Plus material to obtain and alloy having the approximate composition (in weight percent) of 0.09C, 3.9Mn, 0.46Si, 13.1Ni, 20.1Cr, 0.28Mo, 0.008V, 0.77Nb, 0.28N, 2.94Cu, 1W, and the balance Fe.
- Tensile bars were machined from the casting blocks, and tensile tests and creep tests were repeated on this new alloy.
- Table VIII lists the results of these tensile and creep tests. Unexpectedly, the inventors found that adding both the Cu and W together introduced synergistic effects that decreased the creep rate and increased the creep rupture life of the material significantly. Microscopic analyses of this alloy indicated that its microstructure was substantially free of delta ferrite 10 or sigma phases 14 of steel in the as-cast and the post high temperature aged microstructure. TABLE VIII Creep strength (ASTM E139) Creep Tensile tests (ASTM E8 &E12) Creep resistance Temp YS UTS Ductility Stress Temp rupture Creep ductility Min. creep (C.) (Mpa) (Mpa) Elong.
- the disclosed heat and corrosion resistant cast austenitic stainless steel alloy can be used for the production of any articles exposed to extreme temperatures and/or extreme thermal cycling conditions.
- the disclosed alloy can be used for components in engines and power systems.
- the present disclosure is not limited to these applications, as other applications will become apparent to those skilled in the art.
- the improved creep ductility combined with a lower creep rate for CF8C-Plus steel results in increased low cycle fatigue life and creep rupture strength. Increased low cycle fatigue life and creep rupture strength allows components made of CF8C+ to be long lasting.
- the increased creep strength and fatigue life of the disclosed CF8C-Plus steel alloys over traditional CF8C material is unexpected because both these materials are castings, and therefore, deformation processes are not involved in creating a dislocation structure upon cooling.
- Engine and turbine manufacturers may also reduce the weight of components as a result of the increased power density by thinner section designs allowed by increased high temperature strength and corrosion resistance compared to conventional high-silicon molybdenum ductile irons. Further, the stainless steel alloys of the present disclosure provide superior performance over other cast stainless steels for a comparable or lower cost. Finally, stainless steel alloys disclosed herein will assist manufacturers in meeting emission regulations for diesel, turbine and gasoline engine applications.
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Abstract
Description
- This application is a continuation-in-part of U.S. patent application Ser. No. 10/195,724 filed Jul. 15, 2002, the disclosure of which is incorporated by reference herein.
- This invention was made with government support under the terms of Contract No. DE-AC05-960R2264 awarded by the U.S. Department of Energy. The government may have certain rights in this invention.
- This disclosure relates generally to cast austenitic stainless steel alloys of the CF8C type with improved high temperature strength. More particularly, this disclosure relates to CF8C type stainless steel alloys and articles cast therefrom having excellent high temperature creep strength, and aging resistance, and which exhibit a stable austenitic microstructure with substantially no delta ferrite after casting and high temperature aging.
- There is a need for high strength, oxidation resistant and crack resistant cast alloys for use in components subject to extreme temperature environments. Advanced diesel engines must continue to have high fuel efficiency as well as reduced exhaust emissions, without sacrificing durability and reliability. More demanding duty cycles require exhaust manifolds and turbocharger housing materials to withstand temperatures above 750° C. Such materials must withstand both prolonged, steady high-temperature exposure as well as more rapid and severe thermal cycling. New emissions reduction technology and transient power excursions can push temperatures in these critical components even higher. The current material of choice for diesel engine components is Silicon-Molybdenum (SiMo) cast iron. However, it is being pushed beyond its high temperature strength and corrosion limitations. Nickel based super alloys are candidate materials for other high temperature applications like gas turbines, due to its excellent high temperature properties. However, the cost of nickel makes nickel based super alloys expensive, and turbine manufacturers are considering lower-cost alternatives for casings and large structural components. These material issues are not unique to diesel engines and combustion turbines. Distributed power applications that utilize advanced natural gas reciprocating engines need low-cost high-temperature capable materials as expectations for efficiency and service temperature increase. Any new material for these applications should have low cost and good high temperature creep and fatigue resistance.
- Because these components are made by casting processes, any new material should have good casting characteristics like melt fluidity, hot tear resistance, and weldability. A significant factor in the cost of producing a casting is the post casting stress relief or solution heat treatment typically required for stainless steel castings. Eliminating the need for post casting heat treatments can result in substantial time and money savings for casting manufacturers. These cost savings can be even higher for large components like steam turbine casings where large furnaces have to be used. Therefore, any new material should have the desired properties in the as-cast state, that is, without the need for post casting heat treatment.
- CF8C is a commercially available cast austenitic stainless steel that is relatively inexpensive. However, standard practice is to solution treat CF8C castings at 1050° C., which like discussed above, may increase its cost for some applications. Currently-available cast austenitic stainless CF8C steels may include from 18 wt. % to 21 wt. % chromium, 9 wt. % to 12 wt. % nickel and smaller amounts of carbon, silicon, manganese, phosphorous, sulfur and niobium. CF8C typically includes about 2 wt. % silicon, about 1.5 wt. % manganese and about 0.04 wt. % sulfur. CF8C is a niobium stabilized grade of austenitic stainless steel most suitable for applications at temperatures below 500° C. In the standard form CF8C has poor strength at temperatures above 600° C. It also does not provide adequate cyclic oxidation resistance at temperatures exceeding 700° C., does not provide sufficient ductility, does not have the requisite long-term stability of the original microstructure after high temperature aging, and lacks long-term resistance to cracking during severe thermal cycling.
- In austenitic stainless steel castings, such as CF8C, delta ferrite is present in the as-cast microstructure. This delta-ferrite in the microstructure transforms to sigma (σ) phase during prolonged high-temperature exposure, decreasing the ductility of the material, particularly at lower or ambient temperatures. The absence of delta ferrite and sigma phase in the microstructure in the as-cast state and after prolonged exposure to high temperatures (high temperature aging) is an important advantage to preserve the as-cast properties of the material during the lifetime of a component created with the material.
- A class of stainless steel alloys is described in U.S. Pat. No. 5,340,534 issued to Magee (hereinafter, “the '534 patent”.) The '534 patent seeks to improve the galling resistance and corrosion resistance of stainless steel alloys. A concentration of silicon above 2.25% is an important contributor to the improved galling resistance of the alloy. Silicon is also important for metal fluidity of casting steels. However, silicon promotes the formation of ferrite, sigma phases and niobium rich lanes or other silicide phases in the steel, and ferrite volume measurements indicate ferrite volumes between 2.3 and 7 percent in different heats of alloys described in the '534 patent. As described earlier, presence of ferrite and sigma phases deteriorates the properties of steels exposed to high temperatures. Another class of stainless steel alloys is described in U.S. Pat. No. 4,341,555 issued to Douthett et al. (hereinafter, “the '555 patent”.) In the alloys described in the '555 patent, the concentration of carbon is restricted to 0.06%, and a concentration of molybdenum is kept between 2 and 4.5% for good pitting and acid corrosion resistance. The alloys described in the '555 patent rely on post casting stress relief heat treatments to improve their mechanical properties.
- It is, therefore, desirable to have a modified CF8C type steel alloy which has good casting characteristics, improved strength and creep properties at temperatures above 600° C. in the as-cast state, and which exhibits a stable and completely austenitic microstructure after casting and high temperature aging, so that the improved strength and ductility of the material is maintained over the lifetime of the alloy. Completely austenitic microstructure refers to a nearly 100% austenitic microstructure which is substantially free of delta ferrite and sigma phases of steel.
- The disclosed system is directed to overcoming one or more of the problems set forth above.
- In one aspect, the present disclosure is directed to a heat and corrosion resistant cast austenitic stainless steel alloy which contains less than about 15% nickel. The alloy has a completely austenitic microstructure in an as-cast state, and a creep rupture life exceeding 20,000 hrs at a stress of 35 MPa and a temperature of 850° C., when creep tested in the as-cast state under ASTM E139 test conditions.
- In another aspect, the present disclosure is directed to a heat and corrosion resistant cast austenitic stainless steel alloy containing less than 15% nickel. The alloy has a creep rupture life exceeding 3,000 hrs and a minimum creep rate of less than 1×10−3 at a stress of 100 MPa and a temperature of 750° C., when creep tested in the as-cast state under ASTM E139 test conditions. The alloy also has a 0.2% yield strength exceeding 130 MPa at 750° C. in the as-cast state, and a decrease in 0.2% yield strength from 750 to 900° C. of less than 20%; and, a completely austenitic microstructure after casting.
- In another aspect, the present disclosure is directed to an article made of a heat and corrosion resistant cast austenitic stainless steel alloy which contains less than about 15% nickel and has a completely austenitic microstructure. The article also shows no detectable ferromagnetic phases like ferrite or martensite when measured with a measurement device after casting and after high temperature aging for 3000 hrs at 750° C. The article has a creep rupture life exceeding 20,000 hrs at a stress of 35 MPa and a temperature of 850° C., when creep tested in the as-cast state under ASTM El 39 test conditions and a creep rupture life exceeding 2000 hours and a minimum creep rate less than 5×10−3 at a stress of 100 MPa and a temperature of 750° C., when creep tested in the as-cast state under ASTM E139 test conditions.
- The present disclosure also discloses a heat and corrosion resistant cast austenitic stainless steel alloy which has a completely austenitic microstructure in the as-cast state. The alloy includes about 0.05 weight percent to about 0.15 weight percent of carbon, about 1.5 weight percent to about 3.5 weight percent copper, about 0.25 weight percent to about 1.0 weight percent tungsten, and about 0.6 weight percent to about 1.5 weight percent of niobium.
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FIG. 1 a is an SEM micrograph of the microstructure of an exemplary polished and etched as-cast CF8C alloy. -
FIG. 1 b is an SEM micrograph of the microstructure of an exemplary polished and etched as-cast CF8C-Plus alloy. -
FIG. 2 a shows the microstructure of an exemplary CF8C alloy before high temperature aging. -
FIG. 2 b shows the microstructure of an exemplary CF8C alloy after high temperature aging. -
FIG. 3 a shows the microstructure of an exemplary CF8C-Plus alloy before high temperature aging. -
FIG. 3 b shows the microstructure of an exemplary CF8C-Plus alloy after high temperature aging. -
FIG. 4 a is a TEM image of the microstructure of an exemplary CF8C alloy after creep testing at 850° C. and 35 MPa. -
FIG. 4 b is a TEM image of the microstructure of an exemplary CF8C-Plus alloy after creep testing at 850° C. and 35 MPa. - CF8C is the traditional cast equivalent of type 347 stainless steel. The chemistry of CF8C-Plus is based on the composition of CF8C with precise additions of nickel (Ni), manganese (Mn), and nitrogen (N) combined with a reduction in silicon (Si) and adjustments of other minor alloying elements. These alloy modifications were made to improve the high-temperature mechanical properties and the casting characteristics of the CF8C steel using inexpensive alloying elements without the need for post casting heat treatments.
TABLE I Weight percentage (%) Compositional Example range alloy Min Max CF8C CF8C+ Carbon (C) 0.05 0.15 0.07 0.1 Chromium (Cr) 18 25 19 19 Nickel (Ni) 10 15 10 12.5 Niobium (Nb) 0.1 1.5 0.8 0.8 Nitrogen (N) 0.05 0.5 0.25 Manganese (Mn) 0.5 10 1 4 Sulphur (S) 0 0.05 trace trace Molybdenum (Mo) 0 1 0.3 0.3 Phosphorous (P) 0 0.04 trace trace Copper (Cu) 0 3.5 Silicon (Si) 0.2 1 1 0.5 Titanium (Ti) 0 0.2 Cobalt (Co) 0 5 Aluminum (Al) 0 3 Boron (B) 0 0.01 Tungsten (W) 0 3 Vanadium (V) 0 3 Iron (Fe) Balance Balance Balance - Table I is directed towards the maximum and minimum ranges of the compositional elements made in accordance with the present disclosure. Table I also includes (in column labeled “Example alloy”) an example of an embodiment of an alloy made in accordance with the present disclosure. Embodiments covered by the present disclosure include alloys with any subset of compositional ranges falling within the minimum and maximum ranges shown in Table I. It should be noted that allowable ranges of cobalt (Co), vanadium (V), and titanium (Ti) may not significantly alter the performance of the resulting material. Specifically, based upon current information, Co may range from 0 to about 5 weight percent, V may range from 0 to about 3 weight percent, and Ti may range from 0 to about 0.2 weight percent without significantly altering the performance of the alloys.
- To study the effect of these modifications on the mechanical properties and creep behavior of the materials, mechanical testing was carried out, and the test results of the modified alloy (named CF8C-Plus) samples are compared with those of the traditional CF8C steel alloy. Samples of the traditional CF8C and the CF8C-Plus material were cast for experiments using centrifugal casting. Table I also shows the composition of CF8C and CF8C-Plus steel alloys that were used for these studies.
-
FIG. 1 a shows the microstructure of an exemplary polished and etched as-cast CF8C alloy, andFIG. 1 b shows the microstructure of an exemplary polished and etched as-cast CF8C-Plus alloy The microstructure of the as-cast CF8C alloy includes an austenite matrix withdelta ferrite 10 pools in the interdentrite core regions, and niobium carbide (NbC) 12 in the interdentritic regions. In contrast, the microstructure of the as-cast CF8C-Plus alloy does not show anydelta ferrite 10. The microstructure of CF8C-Plus alloy is fully austenitic with a mixture of chromium carbide (Cr23C6) andNbC 12 in the interdentritic regions. A digital Fisher® Feritscope® was used to measure the ferrite content of both the CF8C and CF8C-Plus steel castings. The CF8C had a ferrite number of about 16.8+/−1.1, which is equivalent to about 14% delta ferrite, and the CF8C-Plus did not register any detectable ferromagnetic behavior, meaning it has less than about 0.1% delta ferrite. Both these macroscopic measurements and microscopic studies indicate that the CF8C-Plus material in the as-cast state is substantially free ofdelta ferrite 10 in the as-cast state. - To investigate the microstructural evolution of CF8C and CF8C-Plus steel during aging, sand cast keel bars were encapsulated in quartz tubes, evacuated, and backfilled with argon. These were aged in an air box furnace at 750° C. for 3,000 hours. These specimens were polished and etched for optical microscopy using an etchant composed of glycerin, hydrochloric acid, nitric acid, and acetic acid having a volumetric ratio of 3:3:1:1. Scanning Electron Microscopy (SEM) analysis was performed on polished and unetched specimens using backscatter electron (BSE) imaging, and x-ray energy dispersive spectroscopy (XEDS) was performed on areas of interest.
-
FIG. 2 a shows a BSE image of the microstructure of an exemplary CFSC alloy before high temperature aging, andFIG. 2 b shows a BSE image of the microstructure of an exemplary CF8C alloy after high temperature aging at 750° C. for 3,000 hours. Comparison ofFIGS. 2 a and 2 b indicate a change in BSE image contrast indelta ferrite 10 of the aged material. XEDS analysis of these regions in the aged material indicates that they are enriched in silicon (Si) and chromium (Cr) compared to the delta-ferrite 10 found in the as-cast structure. Comparison ofFIGS. 2 a and 2 b indicates that delta-ferrite 10 has transformed intosigma phase 14 after high temperature aging. Based on the chemical composition of the phase and the knowledge that delta-ferrite 10 can transform rapidly tosigma phase 14 in stainless steels, it is concluded that aging for 3,000 hours at 750° C. transforms a majority of thedelta ferrite 10 in CF8C steel intosigma phase 14. Electron diffraction patterns from these regions were studied using transmission electron microscopy (TEM) and confirmed the presence of body centered tetragonal (bct) sigma phase. -
FIG. 3 a shows a BSE image of the microstructure of an exemplary CF8C-Plus alloy before high temperature aging, andFIG. 3 b shows a BSE image of the microstructure of an exemplary CF8C-Plus alloy after high temperature aging at 750° C. for 3,000 hours. In contrast to the CF8C alloys shown inFIG. 2 a andFIG. 2 b, the CF8C-Plus steel alloys inFIG. 3 a andFIG. 3 b do not show the formation of anydelta ferrite 10 or sigma phases 14 after high temperature aging. The structure of CF8C-Plus alloy before and after high temperature aging samples is austenitic withinterdendritic carbides 16. No obvious change was observed in carbide size or morphology after aging. These studies indicate that in contrast to CF8C alloy, the CF8C-Plus alloy is substantially free ofdelta ferrite 10 or sigma phases 14 of steel after high temperature aging at 750° C. for 3,000 hours. - From the centrifugal castings, tensile, creep, and fatigue specimens were machined in both the hoop and longitudinal orientations. Room temperature and elevated temperature tensile tests were performed in accordance with ASTM E8 and E21. Air creep testing was performed in accordance with ASTM E139 at constant load in lever-arm type creep machines with extensometers attached to the shoulders of the specimens to measure creep deformation. Low cycle fatigue (LCF) and creep-fatigue (C-F) testing was performed in servo-hydraulic test systems in strain control using induction heating in accordance with ASTM E606. For the creep-fatigue tests, a strain hold was imposed at maximum tensile strain during the cycle.
- Table II compares the average tensile properties, namely 0.2% offset yield strength (YS), ultimate tensile strength (UTS), and ductility as measured as the percentage elongation at fracture (Elong.), and percentage reduction of cross sectional area at fracture (RA), for CF8C, and CF8C-Plus (CF8C+) steels as a function of temperature. The average yield strength of CF8C-Plus changes very little above 700° C., while that of CF8C steel shows significant weakening. The average ultimate tensile strength of the CF8C-Plus steel is higher for the entire temperature range compared to CF8C. This increase is significantly higher (>70 Mpa) at temperatures above 700° C. The ductility, as measured by elongation and reduction of area, of CF8C-Plus steel are both higher than that of CF8C steel above 700° C.
TABLE II Tensile tests (ASTM E8 &E12) Ductility Temp YS (Mpa) UTS (Mpa) Elong. (%) RA (%) (C.) CF8C CF8C+ CF8C CF8C+ CF8C CF8C+ CF8C CF8C+ 25 252 273 555 587 41.0 42.5 41.0 34.1 200 184 194 425 473 37.5 40.0 54.0 36.0 400 162 169 415 476 32.0 41.4 55.0 42.5 600 138 143 330 398 34.4 40.0 40.5 45.5 700 136 135 237 324 20.5 32.0 24.0 38.5 750 129 333 29.8 42.5 800 121 136 151 255 11.0 27.4 16.5 43.2 850 132 243 33.4 56.0 900 66 120 73 170 25.5 49.5 43.5 65.5 - Table III compares the average creep rupture life of CF8C and CF8C-Plus (CF8C+) alloys at different stresses and temperatures. As seen in the table, the creep rupture life of CF8C-Plus steel is over an order of magnitude higher than that of CF8C steel in all cases. The creep ductility of CF8C-Plus steel, both as measured as a percentage change in elongation and percentage change in area, also shows a significant improvement over that of CF8C steel. In most cases, this improvement in ductility over CF8C steel is over 100%. The minimum creep rate of CF8C-Plus steel also shows a significant decrease over that of CF8C. In most cases, this decrease in minimum creep rate is over an order of magnitude lower than that of CF8C.
TABLE III Creep strength (ASTM E139) Creep Resistance Creep Creep ductility (%) Minimum Creep Stress Temp rupture life Elong. (%) RA (%) Rate (%/hr) (Mpa) (C.) CF8C CF8C+ CF8C CF8C+ CF8C CF8C+ CF8C CF8C+ 35 850 1159 24100 8.4 7.8 8.3 13.5 75 850 104 28.6 60.9 1.8E−02 100 750 87.4 2443.5 5.9 25.6 4.9 44.6 1.0E−02 2.2E−03 140 750 3.7 120.5 8.2 31.6 12.5 51.1 9.6E−01 1.1E−02 180 650 88.5 3913.2 8.1 20.5 12.4 43.3 2.2E−02 1.0E−04 -
FIG. 4 a is a TEM image of the microstructure of CF8C after 493 hours of creep testing at 850° C. and 35 MPa.FIG. 4 b is the TEM image of the microstructure of CF8C-Plus after over 20,000 hours of creep testing at 850° C. and 35 MPa. Comparison ofFIGS. 4 a and 4 b shows that theNbC 12 precipitates in the CF8C-Plus steel were less than about 50 nanometers in average diameter (as shown inFIG. 4 b,) while the average diameter of these precipitates was over about 250 nanometers, with much larger spacing after only 493 hours of testing, in CF8C alloys (as shown inFIG. 4 a.) - To study the effect on low cycle fatigue, fully reversed (R-ratio=−1) strain controlled low cycle fatigue tests were run at 650° C. and 800° C. at constant frequency. Table IV compares the low cycle fatigue life of CF8C and CF8C-Plus (CF8C+) steels at different strain ranges at the two different temperatures. At 650° C. both materials show similar behavior at high strains, but CF8C-Plus alloys show significant improvement in cycles to failure for the lowest strain ranges. A similar result is found at 800° C.
TABLE IV 650 C. 850 Strain range CF8C CF8C+ CF8C CF8C+ 0.3 30161 >255567 8535 30471 0.5 7333 22545 3392 3826 0.7 7647 4099 2624 2203 1 1794 2396 1394 717 - Additionally, low cycle fatigue tests were run at 750° C. with an R-ratio of 0 to 0.45% strain (0 to 0.45% total strain) at a strain rate of 0.001/sec. For these creep-fatigue experiments, a 180 second hold time at the maximum strain (0.45%) was utilized. Table V shows the results for these tests. For the low cycle fatigue tests, the cycles to failure for the CF8C was 50% that of the CF8C-Plus. Both materials had a reduction in cycle life when the 180 second peak strain hold was added, but the CF8C showed a more dramatic reduction (75%) compared to the CF8C (60%). The creep-fatigue cycle life of the CF8C-Plus steel was three times that of the CF8C steel.
TABLE V Approximate Low cycle cycles to fatigue failure life CF8C CF8C+ Continuous cycle 5000 9750 180 Sec peak 1100 4000 strain hold - The effects of further alloying elements in CF8C-Plus material was also studied. Four separate alloying additions, B, W, Cu, and Al, were chosen for evaluation on CF8C-Plus steel. Fifteen pound lab-scale heats of CF8C-Plus with minor alloy additions were produced by induction melting with an argon cover gas and cast into graphite blocks (152 mm 102 mm×25.4 mm). One heat was cast to the CF8C-Plus composition, and four other heats contained a single alloy addition each. The approximate measured compositions of these five castings (wt %) are given in Table VI. The column titled ‘CF8C+’ lists the approximate composition of an embodiment of an alloy made in accordance with the present disclosure. This alloy is used as the baseline to compare the effect of additional alloying elements in the alloy. The columns titled ‘CF8C+B’, ‘CF8C+W’, ‘CF8C+Cu’, and ‘CF8C+Al’ list the composition of the alloys obtained by adding about 0.005 weight percent of boron, about 0.45 weight percent of tungsten, about 2.5 weight percent of copper, and about 1.3 weight percent of aluminum, respectively, to the composition of the CF8C-Plus alloy.
TABLE VI Approximate weight percent CF8C + CF8C+ B CF8C + W CF8C + Cu CF8C + Al C 0.1 0.1 0.1 0.09 0.01 Mn 4.25 4.25 4.16 4.26 4.44 Si 0.5 0.5 0.5 0.5 0.6 Ni 12.7 12.7 12.6 12.9 12.3 Cr 19.3 19.4 18.9 19.1 19.2 Mo 0.25 0.25 0.25 0.25 0.26 V 0.008 0.01 0.008 0.008 0.008 Nb 0.78 0.79 0.75 0.77 0.8 N 0.28 0.22 0.26 0.25 0.26 Fe Bal Bal Bal Bal Bal Addition .005B .45W 2.5Cu 1.3Al - No post-casting stress-relief or solution annealing treatment was given to these castings. Tensile bars were machined from the casting blocks, and tensile tests and creep tests were performed on these materials. The test condition chosen to screen all the specimens was 850° C. and 75 MPa. Alloy samples that had creep rupture lives comparable to the CF8C-Plus material were then tested at 750° C. and 140 MPa.
- Table VII compares the tensile test and creep test results of the four alloy additions to the CF8C material. As the results indicate, samples with Al and B additions exhibited worse creep life than CF8C-Plus material, and were not, therefore, chosen for creep testing at 750° C. and 140 MPa. The results indicate that the alloys with the Cu and W additions performed better than the base CF8C-Plus material in high temperature creep.
TABLE VII Tensile tests (ASTM E8 &E12) Creep strength (ASTM E139) YS (Mpa) UTS (Mpa) Creep Rupture life (hrs) Alloy 25 C. 850 C. 25 C. 850 C. (850 C., 75 MPa) (750 C., 140 MPa) CF8C-Plus 291 151 655 231 170 320 CF8C-Plus + B 267 145 608 220 85 — CF8C-Plus + W 298 153 604 233 180 340 CF8C-Plus + Cu 283 153 667 231 190 450 CF8C-Plus + Al 227 123 555 176 30 — - Based upon these results, both Cu and W together were added to the CF8C-Plus material to obtain and alloy having the approximate composition (in weight percent) of 0.09C, 3.9Mn, 0.46Si, 13.1Ni, 20.1Cr, 0.28Mo, 0.008V, 0.77Nb, 0.28N, 2.94Cu, 1W, and the balance Fe. Tensile bars were machined from the casting blocks, and tensile tests and creep tests were repeated on this new alloy.
- Table VIII lists the results of these tensile and creep tests. Unexpectedly, the inventors found that adding both the Cu and W together introduced synergistic effects that decreased the creep rate and increased the creep rupture life of the material significantly. Microscopic analyses of this alloy indicated that its microstructure was substantially free of
delta ferrite 10 or sigma phases 14 of steel in the as-cast and the post high temperature aged microstructure.TABLE VIII Creep strength (ASTM E139) Creep Tensile tests (ASTM E8 &E12) Creep resistance Temp YS UTS Ductility Stress Temp rupture Creep ductility Min. creep (C.) (Mpa) (Mpa) Elong. (%) RA (%) (Mpa) (C.) life (hrs) Elong. (%) RA (%) rate (%/hr) 25 252 585 40.0 39.0 75 850 80.4 22.4 43.2 2.80E−03 200 165 475 38.0 41.5 400 145 440 40.5 44.5 600 135 375 37.0 41.0 100 750 3904.4 19.1 32.4 5.10E−04 700 140 310 20.0 18.5 750 150 275 12.0 13.5 800 140 235 13.0 19.5 140 750 289.6 21.1 39.2 2.50E−03 850 150 225 14.0 17.0 900 120 155 36.0 39.0 - The disclosed heat and corrosion resistant cast austenitic stainless steel alloy can be used for the production of any articles exposed to extreme temperatures and/or extreme thermal cycling conditions. The disclosed alloy can be used for components in engines and power systems. However, the present disclosure is not limited to these applications, as other applications will become apparent to those skilled in the art.
- By employing the stainless steel alloys of the present disclosure, manufacturers can provide a more reliable and durable high temperature component. The absence of delta-
ferrite 10 in the microstructure after casting produces a stable austenitic microstructure in CF8C-Plus. Delta-ferrite 10 transforms tosigma phase 14 during prolonged high-temperature exposure causing embrittlement. CF8C-Plus has a nearly 100% austenite microstructure, substantially free of delta ferrite and sigma phase. - The improved creep ductility combined with a lower creep rate for CF8C-Plus steel results in increased low cycle fatigue life and creep rupture strength. Increased low cycle fatigue life and creep rupture strength allows components made of CF8C+ to be long lasting. The increased creep strength and fatigue life of the disclosed CF8C-Plus steel alloys over traditional CF8C material is unexpected because both these materials are castings, and therefore, deformation processes are not involved in creating a dislocation structure upon cooling. Potential reasons for the significant improvement of low cycle fatigue life and creep rupture life of CF8C-Plus over traditional CF8C alloys are that the presence of Mn alters the stacking fault energy of the CF8C-Plus alloy giving rise to higher energy stacking faults, and the presence of manganese and nitrogen in the alloy composition helps nucleation of NbC. The size and density of the
NbC 12 precipitates in the matrix may also contribute to the observed improvement in fatigue life and creep rupture life. The presence of these fine particulates ofNbC 12 could likely pin dislocations, improving the creep rupture life of CF8C-Plus alloys. The increased fatigue and creep rupture life, the decreased creep strain rate, and the lower decrease in 0.2% yield strength at high temperatures may allow engine and turbine manufacturers to increase power density by allowing engines and turbines to run at higher temperatures, thereby providing possible increase in fuel efficiency. - Engine and turbine manufacturers may also reduce the weight of components as a result of the increased power density by thinner section designs allowed by increased high temperature strength and corrosion resistance compared to conventional high-silicon molybdenum ductile irons. Further, the stainless steel alloys of the present disclosure provide superior performance over other cast stainless steels for a comparable or lower cost. Finally, stainless steel alloys disclosed herein will assist manufacturers in meeting emission regulations for diesel, turbine and gasoline engine applications.
- While only certain embodiments have been set forth, alternative embodiments and various modifications will be apparent from the above description to those skilled in the art. These and other alternatives are considered equivalents and within the spirit and scope of the present disclosure.
Claims (22)
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US11/495,671 US20060266439A1 (en) | 2002-07-15 | 2006-07-31 | Heat and corrosion resistant cast austenitic stainless steel alloy with improved high temperature strength |
KR1020097004121A KR20090035723A (en) | 2006-07-31 | 2007-02-28 | Heat and corrosion resistant cast austenitic stainless steel alloy with improved high temperature strength |
RU2009107232/02A RU2009107232A (en) | 2006-07-31 | 2007-02-28 | HEAT- AND CORROSION-RESISTANT CASTING ALLOY OF AUSTENITIC STAINLESS STEEL WITH IMPROVED HIGH-TEMPERATURE STRENGTH |
EP07751919A EP2047007A1 (en) | 2006-07-31 | 2007-02-28 | Heat and corrosion resistant cast austenitic stainless steel alloy with improved high temperature strength |
PCT/US2007/005188 WO2008016395A1 (en) | 2006-07-31 | 2007-02-28 | Heat and corrosion resistant cast austenitic stainless steel alloy with improved high temperature strength |
CNA2007800308824A CN101506399A (en) | 2006-07-31 | 2007-02-28 | Heat and corrosion resistant cast austenitic stainless steelalloy with improved high temperature strength |
JP2009522748A JP2009545675A (en) | 2006-07-31 | 2007-02-28 | Heat and corrosion resistant austenitic stainless steel cast steel alloy with improved high temperature strength |
CA002580933A CA2580933A1 (en) | 2006-07-31 | 2007-03-05 | Heat and corrosion resistant cast austenitic stainless steel alloy with improved high temperature strength |
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Also Published As
Publication number | Publication date |
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RU2009107232A (en) | 2010-09-10 |
CN101506399A (en) | 2009-08-12 |
WO2008016395A1 (en) | 2008-02-07 |
EP2047007A1 (en) | 2009-04-15 |
KR20090035723A (en) | 2009-04-10 |
CA2580933A1 (en) | 2008-01-31 |
JP2009545675A (en) | 2009-12-24 |
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