WO1990004659A1 - ACIER MODIFIE A 1 % DE CrMoV POUR ROTOR - Google Patents

ACIER MODIFIE A 1 % DE CrMoV POUR ROTOR Download PDF

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Publication number
WO1990004659A1
WO1990004659A1 PCT/US1989/004604 US8904604W WO9004659A1 WO 1990004659 A1 WO1990004659 A1 WO 1990004659A1 US 8904604 W US8904604 W US 8904604W WO 9004659 A1 WO9004659 A1 WO 9004659A1
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percent
less
steel
manganese
molybdenum
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PCT/US1989/004604
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English (en)
Inventor
Richard L. Bodnar
Robert I. Jaffee
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Electric Power Research Institute, Inc.
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Publication of WO1990004659A1 publication Critical patent/WO1990004659A1/fr

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    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/18Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/18Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium

Definitions

  • This invention relates to steels, and, more particularly, to an improved 1%CrMoV steel useful in producing large turbine rotors for electrical power generation.
  • the present invention is directed to an improvement in one of these materials, the steel used in rotor forgings.
  • the rotor of a steam turbine used in power generation which may be as large as 200 centimeters diameter a t its Iow pressure end, turns on its shaft at a rate of 3600 revolutions per minute
  • 1%CrMoV a specialty steel known as "1%CrMoV” steel has been developed and used over a period of many years. This steel has acceptable strength, creep resistance, resistance to notch sensitivity, and toughness, which are retained, at gradually reduced levels, during thousands of hours of operation of the rotor.
  • the compositions of the 1%CrMoV steels are specified by ASTM Standard A470 Class 8, as modified by supplements.
  • the composition falls within the range 0.25-0.35 percent carbon, 1.0 percent maximum manganese, 0.15-0.35 percent silicon (with silicon below 0.10 percent permitted in some instances), 0.015 maximum phosphorus, 0.015 maximum sulfur, 0.75 percent maximum nickel, 0.90-1.50 chromium, 1.0-1.5 percent molybdenum, 0.20-0.30 percent vanadium, balance iron totalling 100 percent, with all percentages by weight.
  • the present invention provides a steel which has the favorable strength and creep resistance properties of conventional 1%CrMoV steel, but additionally has better toughness, reduced Fracture Appearance Transition Temperature (FATT), improved hardenability, and reduced susceptibility to temper embrittlement after extended use at elevated temperature.
  • FATT Fracture Appearance Transition Temperature
  • the steel of the invention can be heat treated in a manner similar to that employed for 1%CrMoV steel, but other heat treatments can be employed to further improve the toughness of the steel.
  • the steel of the invention is somewhat more expens ive to produce than the conventional rotor steel, but yields substantially improved properties.
  • a steel consists essentially of from about 0.20 percent to about 0.35 percent carbon, less than about 0.1 percent manganese, from about 0.5 percent to about 6.5 percent nickel, from about 0.8 percent to about 2.0 percent chromium, from about 0.9 percent to about 2.0 percent molybdenum, from about 0.1 percent to about 0.4 percent vanadium, from zero to about 0.07 percent columbium, less than about 0.12 percent silicon, less than about 0.006 percent phosphorus, less than about 0.002 percent sulfur, less than about 0.005 percent antimony, less than about 0.010 percent arsenic, less than about 0.010 percent tin, less than about 0.10 percent copper, less than about 0.010 percent aluminum, balance iron totalling 100 percent, with all percentages by weight.
  • a steel consists essentially of from about 0.20 percent to about 0.35 percent carbon, less than about 0.1 percent manganese, from about 0.5 percent to about 6.5 percent nickel, from about 0.8 percent to about 2.0 percent chromium, from about 0.9 percent to about 2.0 percent molybdenum, from about 0.1 percent to about 0.4 percent vanadium, from zero to about 0.07 percent columbium, less than about 0.12 percent silicon, balance iron totalling 100 percent, with all percentages by weight.
  • This steel is processed to a finished turbine rotor by forging to a preform shape, preliminary heat treating, rough machining, final heat treating, final machining, and inspecting.
  • the preferred preliminary heat treatment includes normalization at 1020 C for 1/2 hour per inch of diameter, cooling, and tempering at about 680 C for 10 hours to soften the steel for ease of machining.
  • the preferred final heat treatment includes austenitizing at 954 C for 1/2 hour per inch of diameter, oil quenching, and tempering at 680 C to a nominal tensile strength of 790 MPa. All heat treatments are normally conducted in suitably controlled furnaces that maintain the necessary heating and cooling rates, and temperatures. Such furnaces may be gas-fired, oil-fired, electric, or otherwise.
  • the atmosphere of heat treatment depends somewhat upon the subsequent processing and the temperatures. Decarburization of the surface, region is to be avoided, if that region is not to be removed by subsequent machining. In such instance, a slightly reducing or inert atmosphere is normally used. If there is to be subsequent machining to remove the surface, heat treating in air is acceptable.
  • a turbine rotor comprises a steel consisting essentially of from about 0.20 percent to about 0.35 percent carbon, less than about 0.1 percent manganese, from about 0.5 percent to about 6.5 percent nickel, from about 0.8 percent to about 2.0 percent chromium, from about 0.9 percent to about 2.0 percent molybdenum, from about 0.1 percent to about 0.4 percent vanadium, from zero to about 0.07 percent columbium, less than about 0.12 percent silicon, balance iron totalling 100 percent, with all percentages by weight.
  • a process for preparing a steel turbine rotor comprises the steps of furnishing a starting material having a composition consisting essentially of from about 0.20 percent to about 0.35 percent carbon, less than about 0.1 percent manganese, from about 0.5 percent to about 6.5 percent nickel, from about 0.8 percent to about 2.0 percent chromium, from about 0.9 percent to about 2.0 percent molybdenum, from about 0.1 percent to about 0.4 percent vanadium, from zero to about 0.07 percent columbium, less than about 0.12 percent silicon, less than about 0.006 percent phosphorus, less than about 0.002 percent sulfur, less than about 0.005 percent antimony, less than about 0.010 percent arsenic, less than about 0.010 percent tin, less than about 0.10 percent copper, less than about 0.010 percent aluminum, balance iron totalling 100 percent, with all percentages by weight; heat treating the starting material; and forming the heat treated starting material into a turbine rotor.
  • Heat treating and forming steps may be, and typically are, intermixed, so that a heat treatment step may be followed by a forming step, which is then followed by another heat treatment step and another forming step.
  • "Forming" is used herein in a broad sense, to Include forging, machining, and other types of metalworking operations.
  • compositions of the steel are preferred as having the most favorable combination of properties, and are favored in the fabrication of a turbine rotor.
  • a steel contains about 0.30 percent carbon, 0.02 percent manganese, about 0.02 percent silicon, about 0.001 percent phosphorus, about 0.001 percent sulfur, about 2.5 percent nickel, about 1.1 percent chromium, about 1.2 percent molybdenum, about 0.25 percent vanadium, and about 0.04 percent columbium.
  • a steel contains about 0.30 percent carbon, 0.02 percent manganese, about 0.02 percent silicon, about 0.001 percent phosphorus, about 0.001 percent sulfur, about 2.5 percent nickel, about 1.5 percent chromium, about 1.4 percent molybdenum, and about 0.25 percent vanadium.
  • a steel contains about 0.30 percent carbon, 0.02 percent manganese, about 0.02 percent silicon, about 0.001 percent phosphorus, about 0.001 percent sulfur, about 2.5 percent nickel, about 1.5 percent chromium, about 1.4 percent molybdenum, about 0.25 percent vanadium, and about 0.04 percent columbium.
  • a steel contains about 0.23 percent carbon, 0.02 percent manganese, about 0.02 percent silicon, about 0.001 percent phosphorus, about 0.001 percent sulfur, about 2.5 percent nickel, about 1.5 percent chromium, about 1.4 percent molybdenum, about 0.25 percent vanadium, and about 0.04 percent columbium.
  • each steel has less than about 0.006 percent phosphorus, less than about 0.002 percent sulfur, less than about 0.005 percent antimony, less than about 0.010 percent arsenic, less than about 0.010 percent tin, less than about 0.10 percent copper, less than about 0.010 percent aluminum.
  • the manganese content is maintained at a relatively low level of less than about 0.1 percent, to avoid the incidence of manganese-related temper embrittlement during extended elevated temperature exposure.
  • a high nickel level is added to compensate for the low manganese content, thereby maintaining the hardenability of the steel and permitting a high level of toughness to be attained by lowering the bainite start temperature and thence the FATT.
  • Silicon is also maintained at a low level to avoid temper embrittlement and the formation of silicate inclusions which would reduce the toughness of the steel.
  • columbium also known as niobium
  • columbium carbides that inhibit austenite grain growth, thus improving the creep resistance and toughness of the steel.
  • Softening resistance is also imparted by the columbium addition.
  • Other elements such as phosphorus, antimony, arsenic, tin are maintained at low levels to avoid temper embrittlement.
  • the sulfur level is low to avoid formation Of sulfides that could lead to hot shortness and reduced toughness.
  • the copper and aluminum contents are low to maintain creep ductility at elevated temperatures. The bases for specific limits on these and other alloying additions will be discussed subsequently.
  • the steels of the invention thus achieve acceptable strength, creep, and toughness properties, while at the same time having improved resistance to degradation of these properties with extended elevated temperature exposure.
  • the FATT can be lowered to below ambient temperature, so that special startup and shutdown procedures are not required, an important saving to the utilities.
  • larger diameter rotor forgings may be hardened throughout their thickness as a result of the improved hardenability of the steei of the invention, as compared with the conventional
  • Figure 1 is a perspective view of a forged steam turbine rotor shaft
  • Figure 2 is a graph of temperature versus time, illustrating the preferred preliminary heat treatment used in treating the preferred steel compositions.
  • Figure 3 is a graph of temperature versus time, illustrating the preferred final heat treatment used in treating the preferred steel compositions.
  • a rotor 10 includes an integral shaft 12 and integral turbine disks 14.
  • the shaft length is typically from 250 to 500 centimeters, and the maximum diameter of the disks is typically from 80 to 200 centimeters.
  • the shaft 12 turns on bearings (not shown).
  • the rotor 10 When the rotor 10 is in service, it is heated by its surroundings and conduction of heat from the turbine blades 18, which are heated by the impinging steam.
  • the rotor 10 turns in the bearings at a high rate, for example 3600 revolutions per minute (in United States practice).
  • the resulting centrifugal forces create high radially outward loads in the rotor 10, which must be sustained for extended periods of time at elevated temperatures of as much as 565 C. Creep of the material in the rotor 10 would cause it to become distorted in shape, reducing its performance or even causing it to rub against its housing.
  • a failure mechanism under these circumstances would be the initiation and propagation of a crack, causing a piece of the rotor to possibly separate and fly radially outwardly. If this were to happen, the remainder of the rotor would become unbalanced and tear out of the bearings, causing a failure of the entire turbine.
  • the rotor has been constructed of a 1%CrMoV steel, whose composition has been previously discussed. Large ingots of the 1%CrMoV steel are heated, forged, preliminary heat treated, rough machined, further heat treated, and final machined to the shape generally illustrated in Figure 1.
  • This steel has proved highly effective in the manufacture of large turbine rotors, and rotors made of the steel are in use throughout the world. However, it is often possible to further improve even successful and useful materials, and the present invention provides such an improvement.
  • the carbon content ranges from about 0.20 percent to about 0.35 percent by weight (all percentages herein are by weight, unless an indication to the contrary is stated). If the carbon content is below about 0.20 percent, the steel is expected to have insufficient creep strength and insufficient hardenability, especially in thick sections. The latter is an Important consideration for steels used in thick sections such as rotors, because acceptable properties must be attained even at the center of a thick piece of steel. If the carbon content is above about 0.35 percent, the microstructure contains too high a volume fraction of carbides formed by reaction of the carbon with metallic elements such as chromium, molybdenum, vanadium, and columbium, present in the steel. The excessive fraction of carbides can assist in the premature initiation of cracks in the steel during loading, reducing its toughness, another important consideration for a steel that is to be used for long periods of loading at elevated temperature.
  • the manganese content of the steel of the invention is less than about 0.10 percent, and preferably less than about 0.05 percent. Most preferably, the manganese content is about 0.02 percent. Desirably, the content of manganese is as low as possible, but it is not generally possible to reach zero manganese in economical commercial production.
  • ASTM Specification A470 for 1%CrMoV steel permits as much as 1.0 percent manganese, and manganese contents of about 0.75 percent are commonly found in steels used In rotors.
  • a word concerning the significance of the specification level for manganese, as well as other alloying additions, is appropriate. The specification is used In commercial melting practice as the limit to which the particular alloying element may be taken.
  • the low level of manganese in the steel of the invention reduces the Incidence of temper embrittlement of the steel, as compared with steels containing higher manganese contents.
  • Temper embrittlement is a phenomenon observed in alloy steels wherein residual elements such as phosphorus can segregate to prior austenite grain boundaries during elevated temperature exposure or cooling from an elevated temperature, and lower their cohesive strength, thus embrittling the steel.
  • Manganese has been identified by the present inventors as a contributor to temper embrittlement by both promoting the grain boundary segregation of residual elements such as phosphorus, as well as itself segregating to grain boundaries and causing their embrittlement.
  • the level of manganese in the steel of the invention has therefore been drastically reduced as compared with prior 1%CrMoV steels.
  • Manganese has beneficial effects upon the steel in avoiding hot shortness, contributing to hardenability, and reducting B s temperature, however, and its removal to low levels, has not heretofore been possible without the loss of desirable features. As will be discussed, the types and levels of other alloying additions have been modified to compensate for the removal of manganese.
  • the silicon content of the present steel is less than about 0.12 percent, preferably less than about 0.05 percent, and most preferably about 0.02 percent.
  • the silicon level is maintained at a low level to avoid the formation of silicate inclusions during steelmaking as well as contributing to the temper embrittlement process, and levels within the specified ranges have been found most effective in minimizing these problems.
  • levels of 0.15 to 0.35 percent are permitted by ASTM Specification A470, although levels below 0.10 percent are permitted by the specification when using vacuum carbon deoxidation.
  • the prior steel and specification do not teach the necessity of keeping the silicon level low.
  • vacuum deoxidation is preferably employed to avoid the need for silicon deoxidation.
  • the chromium content in the steel of the invention ranges from about 0.8 percent to about 2.0 percent, most preferably from about 1.1 percent to about 1.7 percent. If the chromium content is lower than about 0.8 percent, there Is a significant loss in creep strength due to insufficient formation of carbides as well as a reduction of the solid solution strengthening effect of the chromium. If the chromium content is higher than about 2.0 percent, creep strength is lost due to the excessive formation of chromium-containing carbides, which reduces the of carbon available for the formation of finer vanadium-rich carbides, which improve creep strength.
  • the molybdenum content in the steel of the Invention ranges from about 0.9 percent to about 2.0 percent, most preferably from about 1.2 percent to about 1.6 percent.
  • the behavior of molybdenum is similar to that of chromium. If the molybdenum content Is lower than about 0.9 percent, there is a significant loss in creep strength due to insufficient formation of carbides and reduced solid solution strengthening by molybdenum. If the molybdenum content is higher than about 2.0 percent, creep strength is lost due to the excessive formation of molybdenum-containing carbides, which similarly reduces the amount of carbon available for the formation of vanadium-rich carbides.
  • the nickel content of the steel of the invention is from about 0.5 percent to about 6.5 percent, most preferably about 2.5 percent.
  • the inventors have established the following empirical relation for the temperature (degrees C) at which the bainite reaction starts, B s , as a function of the percentage content of carbon by weight (%C), percentage content of nickel by weight (%Ni), percentage content of chromium by weight (%Cr), and percentage content of molybdenum by weight (%Mo), during continuous cooling of the steel of the invention:
  • B s (C) 692 - 217 ( %C ) - 32 (%Ni) - 25 (#Cr + %Mo).
  • the lowest B s temperature acceptable for formation of bainite of the proper microstructure is observed to be about 400 C.
  • the top end of the B s temperature range which provides a suitable bainitic microstructure has been established to be about 500 C.
  • 500 C for the bainite start temperature and the top of the range values for carbon, chromium, and molybdenum the lower value of nickel of about 0.5 percent is established.
  • the nickel content Is used to adjust the bainite start temperature to achieve the most desirable type of microstructure, after the content of the other contributing alloying elements are established.
  • a steel with a lower B s temperature exhibits a finer bainitic microstructure which. provides better toughness than a steel with a higher B s temperature.
  • Nickel has not been identified as causing the formation of damaging phases or depriving the material of critical elements needed for combination with other alloying elements.
  • an addition of nickel can compensate for a reduction of manganese in determining the B s temperature.
  • this "compensation" relation Is such that the compensating addition of nickel must be about four times the reduction of manganese, when each element is expressed as a percentage by weight.
  • the vanadium content is from about 0.1 percent to about 0.4 percent, preferably about 0.25 percent.
  • Vanadium Is an important alloying element, in that fine vanadium-rich carbides (or carbonitrides) formed during heat treatment provide creep strength to the steel.
  • a steel containing less than about 0.1 percent vanadium will not be able to form a sufficient amount of vanadium-rich carbides to achieve acceptable creep strength.
  • a steel containing more than about 0.4 percent vanadium has a high creep strength, but forms .such a high volume fraction of vanadium-rich carbide that the toughness Is unacceptably reduced.
  • Columbium (also known as niobium) is present in an amount of from 0 to about 0.07 percent, preferably from about 0.02 percent to about 0.07 percent, and most preferably about 0.04 percent. Columbium forms fine columbium carbides during heat treatment. The columbium carbides refine the austenitic grain structure of the steel, increasing its toughness and resistance to creep notch sensitivity. An absence of columbium results in the formation of no columbium carbide, while columbium in an amount of from 0 to about 0.02 percent forms a marginally small amount. A columbium content greater than about 0.07 percent results in the formation of eutectic columbium carbide as coarse particles during solidification, resulting in reduced toughness of the final product.
  • temper embrittlement Several minor elements are known to contribute to temper embrittlement during extended exposure. Their levels are therefore maintained as low as possible, consistent with commercial practice, to avoid temper embrittlement. Phosphorus is limited to less than about 0.006 percent, antimony is limited to less than about 0.005 percent, arsenic is limited to less than about 0.010 percent, and tin is limited to less than about 0.010 percent.
  • the sulfur content of the steel is restricted to a low level, less than about 0.002 percent.
  • the ASTM A470 specification permits as much as 0.015 percent sulfur, but in the present steel the sulfur content is held well below that amount.
  • the sulfur forms manganese sulfides, which are relatively harmless but can lead to reduced toughness.
  • the manganese is largely removed, and the sulfur therefore would form an iron sulflde, unless the amount of sulfur is restricted.
  • the presence of iron sulflde precipitates lead to hot shortness of the steel, a highly undesirable characteristic.
  • the sulfur is restricted to a much lower level than in conventional 1%CrMoV steels, due to the reduction of the manganese level.
  • the sulfur content can act as crack Initiation sites and reduce toughness. Improved toughness is achieved when the sulflde volume fraction is reduced by lowering the sulfur content.
  • the copper content is maintained at less than about 0.10 percent, and the aluminum content is maintained at less than about 0.010 percent. Both copper and aluminum can have adverse effects on the creep ductility of the steel. Too high a content of either element, above the indicated limit, may lead to a significant loss of creep ductility, resulting in creep embrittlement.
  • the steels of the present invention are preferably used in the fabrication of rotors, as discussed previously.
  • the following provides a preferred processing procedure, although other procedures are acceptable as long as they obtain similar results.
  • a melted and cast ingot of the steel is forged to approximately the proper shape and size required for the final product, but is left oversize to accommodate rough and final machining.
  • the forged ingot (termed a "forging") is given a preliminary thermal treatment, as illustrated in Figure 2.
  • the temperatures in Figures 2 and 3, and discussed herein, are selected as representative of a typical acceptable commercial practice.
  • the required soaking times, and heating and cooling rates (cooling medium) are applied to particular-sized forgings in the manner known to those skilled in the art.
  • the steel is preferably normalized by heating the forging to 700 C, and then controllably heating the forging at a rate of about 17 C per hour to a normalization temperature of 1020 C.
  • the forging is maintained at 1020 C for 1/2 hour per inch of diameter of the forging, and then air cooled.
  • the normalized steel is tempered by heating it to about 315 C, and controllably heating the forging at a rate of about 17 C per hour to 680 C, where it is maintained for several hours.
  • the forging is air cooled to ambient temperature.
  • the normalized and tempered forging is rough machined as required.
  • the forging is then heat treated for austenitizing and tempering, as schematically Illustrated in Figure 3. Again, the temperatures are those that would be chosen for commercial practice.
  • the steel forging is preferably heated to 700 C, and then controllably heated at a rate of 17 C per hour to an austenitizing temperature of 954 C, where it is maintained for 1/2 hour per inch of diameter.
  • the forging is then cooled, to ambient temperature.
  • Normal commercial practice as presently used in the United States calls for fan cooling, producing a cooling rate of about 50 C per hour at the center of a 127 centimeter di ameter forging .
  • the present steel may be cooled by oil quenching, the preferred process, which produces a cooling rate of about 117 C per hour in the center of a 127 centimeter diameter forging.
  • the oil cooled structure can produce properties superior to those of the fan cooled material.
  • the steel may also be cooled by water, quenching in a bath, spray, or the like, which produces a cooling rate of about 200 C her hour in the center of a 127 diameter forging. Other quenching media are also acceptable.
  • the austenitized rotor is tempered by heating it to 315 C, and controllably heating it to 680 C at a rate of 17 C per hour.
  • the steel is maintained at the tempering temperature to reduce its strength to a specific design limit, which is preferably about 790 MPa.
  • the tempering time for the 127 centimeter diameter forging is about 25 hours.
  • the tempered rotor is cooled to ambient temperature. The rotor is final machined and inspected, and is ready for attachment of the turbine blades (which are separately produced).
  • the rotor made of conventional 1%CrMoV steel is In a generally more brittle state at ambient or room temperature. If the rotor is started up under full power from a cold start, it may fail prematurely in the more brittle state. To avoid the possibility of such failures, the operating practice for such rotors requires a slow and prolonged heating to a temperature above the FATT, before a higher heating rate and higher stress operation is permitted. Similarly, when the rotor is shut down, a carefully controlled, prolonged cooiing procedure is required at temperatures below the FATT. The imposition of these special startup and shutdown procedures is costly due to higher capital and fuel costs, and reduces flexibility of operation.
  • a major objective of the present invention Is therefore to reduce the FATT of the steel to about ambient temperature, or to below ambient temperature.
  • the special startup and shutdown procedures for the rotor to avoid high loading in the more brittle regime, Is not required.
  • Reduction of the FATT is essentially a modification of the hardenability and B s temperature of the steel, which modifications have been described above in relation to the effects of the various alloying elements, taken in combination. As Indicated previously, it is not the effect of any one element and its compositional limitations that produces this Improvement in FATT, but the effects in combination of the several alloying elements that work together to control the properties of the steel.
  • compositional limitations of the present steel permit the FATTs to be reduced to acceptably low temperatures.
  • a steel was prepared having the following composition: 0.30 percent carbon, 0.02 percent manganese, 0.02 percent silicon, 0.001 percent phosphorus, 0.001 percent sulfur, 2.50 percent nickel, 1.50 percent chromium, 1.40 percent molybdenum, and 0.25 percent vanadium, 0.0005 percent antimony, 0.001 percent arsenic, 0.002 percent tin, balance iron plus conventional amounts of impurity elements.
  • the steel was prepared as a 225 kilogram vacuum induction melt, cast into an ingot mold, and hammer forged to a plate measur ing 3 . 5 centimeter s th i ck and 15 . 0 centimeters wide.
  • the plates were given the preferred thermal treatments of normalizing and tempering ( Figure 2, and described above) and austenitizing and tempering to a nominal strength of 790 MPa ( Figure 3, and described above), under simulated fan cooling conditions of a cooling rate of about 50 C per hour from the austenitizing temperature.
  • the FATT of this steel was measured to be 27 C, which is approximately ambient temperature.
  • the bainite start temperature was reduced due to the alloying additions, resulting in improved toughness and the reduced FATT.
  • the creep rupture strength of the steel was superior to that of conventional 1%CrMoV steels.
  • Example 1 was repeated, except that simulated oil quenching, at a cooling rate of about 117 C per hour from the austenitizing temperature, was used during austenitizing and tempering.
  • the FATT was measured as 2 C.
  • Example 1 was repeated, except that the following elements were present in the Indicated amounts: 1.10 chromium rather than 1.50 chromium as in Example 1, 1.20 molybdenum rather than 1.40 molybdenum as in Example 1, and columbium was present in an amount of .04 percent.
  • the FATT of this steel was measured to be 49 C, significantly better than the FATT of conventional 1%CrMoV steels, but still above ambient temperature.
  • the presence of the columbium is observed to reduce the austenitic grain size, resulting in improved toughness of the steel.
  • the creep rupture strength of the steel is superior than that of the conventional 1%CrMoV steel.
  • This steel was tested for temper embrittlement by exposing it to a temperature of 480 C for over 10,000 hours, and was found to be without incidence of temperature embrittlement.
  • Example 3 was repeated, except that the chromium content was increased to 1.50 percent and the molybdenum content was increased to 1.40 percent.
  • the FATT for this steel was measured as 4 C, well below ambient temperature. This steel exhibited creep rupture strength comparable with that of conventional 1%CrMoV steel.
  • Example 4 was repeated, except that the carbon content was decreased to 0.23 percent, from 0.30 percent, and the simulated oil quenching processing was used (as described in relation to Example 2).
  • the FATT was measured as 21 C, below ambient temperature. This steel exhibited creep rupture strength in excess of that of conventional 1%CrMoV steel.
  • the steel of the invention provides an. important advance in the art, particularly for steels used in rotors of steam and gas turbines. These steels have acceptable strength and ductility properties, and good creep and toughness properties, at elevated temperatures. They are resistant to degradation by temper embrittlement. Significantly, their FATTs are reduced below those of prior 1%CrMoV rotor steels, meaning that rotors produced using the steels of the invention need not undergo the extensive startup and shutdown procedures required of the prior rotors.

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Abstract

Un acier modifié à 1 % de CrMoV s'utilisant en particulier pour les rotors de turbine à gaz et à vapeur contient, en pourcentages pondéraux, de 0,20 à 0,35 environ de carbone, moins de 0,1 environ de manganèse, de 0,5 à 6,5 environ de nickel, de 0,8 à 2,0 environ de chrome, de 0,9 à 2,0 environ de molybdène, de 0,1 à 0,4 environ de vanadium, de 0 à 0,07 environ de colombium, moins de 0,12 environ de silicium, moins de 0,006 environ de phosphore, moins de 0,002 environ de soufre, moins de 0,005 environ d'antimoine, moins de 0,010 environ d'arsenic, moins de 0,010 environ d'étain, moins de 0,10 environ de cuivre, moins de 0,010 environ d'aluminium, le reste jusqu'à 100 % étant du fer. Des compositions sélectionnées de cet acier peuvent être traitées pour avoir une température de transition d'apparence de fracture de 50 % inférieure à la température ambiante et ne présente pas de cassure à la trempe après des périodes prolongées d'exposition à des températures élevées. Les propriétés de rupture par fluage et d'aptitude à la trempe de l'acier modifié sont meilleures ou équivalentes à celles des aciers standard à 1 % de CrMoV qui sont cassants à des températures ambiantes et soumis à une fragilisation lors de la trempe.
PCT/US1989/004604 1988-10-19 1989-10-19 ACIER MODIFIE A 1 % DE CrMoV POUR ROTOR WO1990004659A1 (fr)

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US260,245 1988-10-19

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Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0505085A1 (fr) * 1991-03-20 1992-09-23 Hitachi, Ltd. Acier pour arbre d'induit de machines électriques
EP0719869A1 (fr) * 1994-12-26 1996-07-03 The Japan Steel Works, Ltd. Procédé de fabrication d'un rotor monobloc de turbines à haute et basse pression
WO1997022727A1 (fr) * 1995-12-20 1997-06-26 Parsons Chain Company Limited Composition d'alliage d'acier et elements de chaine fabriques dans un tel alliage

Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
GB1009924A (en) * 1962-06-29 1965-11-17 Republic Steel Corp Steel alloys and methods of making same
JPS6070166A (ja) * 1983-09-26 1985-04-20 Hitachi Ltd 耐クリ−プ耐酸化性低合金鋼
JPS60224766A (ja) * 1984-04-23 1985-11-09 Toshiba Corp 蒸気タ−ビンロ−タ

Patent Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
GB1009924A (en) * 1962-06-29 1965-11-17 Republic Steel Corp Steel alloys and methods of making same
JPS6070166A (ja) * 1983-09-26 1985-04-20 Hitachi Ltd 耐クリ−プ耐酸化性低合金鋼
JPS60224766A (ja) * 1984-04-23 1985-11-09 Toshiba Corp 蒸気タ−ビンロ−タ

Cited By (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0505085A1 (fr) * 1991-03-20 1992-09-23 Hitachi, Ltd. Acier pour arbre d'induit de machines électriques
US5288455A (en) * 1991-03-20 1994-02-22 Hitachi, Ltd. Steel for rotor shafts of electric machines and method and product thereof
EP0719869A1 (fr) * 1994-12-26 1996-07-03 The Japan Steel Works, Ltd. Procédé de fabrication d'un rotor monobloc de turbines à haute et basse pression
US5716468A (en) * 1994-12-26 1998-02-10 The Japan Steel Works, Ltd. Process for producing high-and low-pressure integral-type turbine rotor
WO1997022727A1 (fr) * 1995-12-20 1997-06-26 Parsons Chain Company Limited Composition d'alliage d'acier et elements de chaine fabriques dans un tel alliage
US6146583A (en) * 1995-12-20 2000-11-14 Parsons Chain Company Limited Alloy steel composition and chain products fabricated in such alloy steel

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