CN1749427A - Heat-resisting steel, heat treatment method for heat-resisting steel and high-temperature steam turbine rotor - Google Patents
Heat-resisting steel, heat treatment method for heat-resisting steel and high-temperature steam turbine rotor Download PDFInfo
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- CN1749427A CN1749427A CNA2005101096888A CN200510109688A CN1749427A CN 1749427 A CN1749427 A CN 1749427A CN A2005101096888 A CNA2005101096888 A CN A2005101096888A CN 200510109688 A CN200510109688 A CN 200510109688A CN 1749427 A CN1749427 A CN 1749427A
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Abstract
A heat-resisting steel consisting of, in percentage by weight, 0.25 to 0.35 of C, 0.15 or less of Si, 0.2 to 0.8 of Mn, 0.3 to 0.6 of Ni, 1.6 to 1.9 of Cr, 0.26 to 0.35 of V, 0.6 to 0.9 of Mo, 0.9 to 1.4 of W, less than 0.01 of Ti, 0.001 to 0.007 of N, 1.3 to 1.4 of a total of Mo and W/2 and the balance of Fe and inevitable impurities, wherein the heat-resisting steel consists of a bainite single phase structure securing 3.5 or more of a total amount of precipitates as 1.0 or more of Fe, 0.8 to 0.9 of Cr, 0. 4 to 0. 5 of Mo, 0. 3 to 0.5 of W and 0.2 or more of V in percentage by weight are moved into the precipitates after a tempering heat treatment.
Description
The cross reference of related application
The application is based on the Japanese patent application of submitting on September 16th, 1 2004-269947 number and require its right of priority; Its full content is incorporated into here as a reference.
Technical field
The present invention relates to a kind of high temperature steel, more specifically relate to have outstanding properties as the high temperature steel of generating set member such as high-temperature steam turbine rotor material and steam turbine, the heat treating method and the high-temperature steam turbine rotor of high temperature steel.
Background technology
As the high-temperature component material that is used for steam power plant, use in large quantities with the 1Cr-1Mo-0.25V steel as the Mayari of representative with the high Cr high temperature steel of 12Cr-1Mo-VNbN steel as representative.But, in recent years because the steam power plant requirement makes vapor temperature rise De Genggao soon, so increase for the use of high Cr high temperature steel with outstanding high-temperature behavior.
Simultaneously, owing to require steam power plant must have high efficient and economical efficiency in recent years, therefore, expectation uses the high temperature steel of cheapness and excellent performance as component materials.
The parts that constitute the steam power plant centre portions are formed by large-sized material, and this just must require is being excellent aspect the formability of throughput and the desired shape of formation.And, also can not damage under the situation of big parts but keep uniform material property even require them to have forming.Yet, for example, containing at Japanese Patent the 3rd, 334, traditional high temperature steel of disclosed chemical ingredients is wanting in the quenching performance when as big parts in No. 217, and almost can not be in the performance of the centre portions performance expection with swift diameter steel ingot.Contain at Japanese Patent the 3rd, 439, the high temperature steel of No. 197 disclosed chemical ingredientss has sizable component precipitation when the big steel ingot of casting, and almost can not bring into play uniform material property in whole steel ingot.When using special dissolving to improve the homogeneity of steel ingot, high temperature steel has the shortcoming of the economical efficiency that comprises that advantages and disadvantages is for example poor.
Traditional high temperature steel comprises a large amount of relatively ferrite formers, and as strengthening element, the tendency that therefore produces ferritic phase becomes very high as Cr, Mo and W.Usually, the ferritic phase that is produced in mutually at bainite is formed by the Chemical bond of above-mentioned ferrite former and Fe.Therefore, the conduct that these added strengthens the element concentration of local of element in the ferrite that produces, and has the shortcoming that constituent content reduces in the bainite structure, so especially makes hot strength reduce.In addition, when the amount of ferritic phase generation in the high temperature steel increased, the impact property of material or toughness may descend significantly.
Summary of the invention
According to one aspect of the present invention, provide a kind of can stably being used in the high-temperature steam environment and having the high temperature steel of outstanding economical efficiency, heat treating method and a kind of high-temperature steam turbine rotor of this high temperature steel of bainite phase structure that have.
High temperature steel of the present invention is by weight percentage by 0.25～0.35 C, 0.15 or Si still less, 0.2～0.8 Mn, 0.3～0.6 Ni, 1.6～1.9 Cr, 0.26～0.35 V, 0.6～0.9 Mo, 0.9～1.4 W, be less than 0.01 Ti, 0.001～0.007 N, total amount is that the Fe and the unavoidable impurities of 1.3～1.4 Mo and W/2 and surplus formed, wherein after tempering heat treatment, this high temperature steel is made up of the bainite single phase structure, guarantee by weight percentage as 1.0 or more Fe, 0.8～0.9 Cr, 0.4～0.5 Mo, 0.3～0.5 W and 0.2 or more V move into throw out, and the throw out total amount is 3.5 or higher.
High temperature steel of the present invention is by weight percentage by 0.25～0.35 C, 0.15 or Si still less, 0.2～0.8 Mn, 0.3～0.6 Ni, 1.6～1.9 Cr, 0.26～0.35 V, 0.6～0.9 Mo, 0.9～1.4 W, be less than 0.01 Ti, total amount is that the Fe and the unavoidable impurities of 1.3～1.4 Mo and W/2 and surplus formed, wherein after tempering heat treatment, this high temperature steel is made up of the bainite single phase structure, guarantee by weight percentage 1.0 or more Fe, 0.8～0.9 Cr, 0.4～0.5 Mo, 0.3～0.5 W and 0.2 or more V move into throw out, and the throw out total amount is 3.5 or higher.
High temperature steel of the present invention is by weight percentage by 0.25～0.35 C, 0.15 or Si still less, 0.2～0.8 Mn, 0.3～0.6 Ni, 1.6～1.9 Cr, 0.26～0.35 V, 0.6～0.9 Mo, 0.9～1.4 W, 0.001～0.007 N, total amount is that the Fe and the unavoidable impurities of 1.3～1.4 Mo and W/2 and surplus formed, wherein after tempering heat treatment, this high temperature steel is made up of the bainite single phase structure, guarantee by weight percentage 1.0 or more Fe, 0.8～0.9 Cr, 0.4～0.5 Mo, 0.3～0.5 W and 0.2 or more V move into throw out, and the throw out total amount is 3.5 or higher.
According to above-mentioned high temperature steel, the high temperature steel of being made up of the bainite single phase structure can form by the content range internal shaping at the one-component element.Like this, it is excellent and do not contain reduce the ferritic phase of the mechanical property of materials or the high temperature steel of analogue greatly when the amount increase that produces to can be provided in high-temperature behavior, toughness, embrittlement performance or the like aspect.Above-described component element Ti and/or N can be replaced by Fe and C.
The heat treating method that is used for high temperature steel of the present invention comprises by weight percentage by 0.25～0.35 C, 0.15 or still less Si, 0.2～0.8 Mn, 0.3～0.6 Ni, 1.6～1.9 Cr, 0.26～0.35 V, 0.6～0.9 Mo, 0.9～1.4 W, to be less than 0.01 Ti, 0.001～0.007 N, total amount be that 1.3～1.4 Mo and the Fe of W/2 and surplus and the steel ingot that unavoidable impurities is formed are heated to 980～1030 ℃, cooling is carried out temper then so that the speed of cooling of steel ingot centre portions becomes at least 20 ℃/h or more.
The heat treating method that is used for high temperature steel of the present invention comprises by weight percentage by 0.25～0.35 C, 0.15 or still less Si, 0.2～0.8 Mn, 0.3～0.6 Ni, 1.6～1.9 Cr, 0.26～0.35 V, 0.6～0.9 Mo, 0.9～1.4 W, to be less than 0.01 Ti, total amount be that 1.3～1.4 Mo and the Fe of W/2 and surplus and the steel ingot that unavoidable impurities is formed are heated to 980～1030 ℃, cooling is carried out temper then so that the speed of cooling of steel ingot centre portions becomes at least 20 ℃/h or more.
The heat treating method that is used for high temperature steel of the present invention comprise with by weight percentage by 0.25～0.35 C, 0.15 or still less Si, 0.2～0.8 Mn, 0.3～0.6 Ni, 1.6～1.9 Cr, 0.26～0.35 V, 0.6～0.9 Mo, 0.9～1.4 W, 0.001～0.007 N, total amount be that 1.3～1.4 Mo and the Fe of W/2 and surplus and the steel ingot that unavoidable impurities is formed are heated to 980～1030 ℃, cooling is carried out temper then so that the speed of cooling of steel ingot centre portions becomes at least 20 ℃/h or more.
According to the above-mentioned heat treating method that is used for high temperature steel, even be at least 20 ℃/h or higher speed of cooling is implemented to quench and do not force cooling by for example heat-eliminating medium Ru Shui, oil or analogue or air blast with low-down at the steel ingot centre portions, also can form the high temperature steel that comprises the bainite single phase structure that does not form ferritic phase.
High-temperature steam turbine rotor of the present invention comprises by weight percentage by 0.25～0.35 C, 0.15 or Si still less, 0.2～0.8 Mn, 0.3～0.6 Ni, 1.6～1.9 Cr, 0.26～0.35 V, 0.6～0.9 Mo, 0.9～1.4 W, be less than 0.01 Ti, 0.001～0.007 N, total amount is 1.3～1.4 Mo and the Fe of W/2 and surplus and the high temperature steel that unavoidable impurities is formed, wherein after tempering heat treatment, this high temperature steel is made up of the bainite single phase structure, guarantee by weight percentage 1.0 or more Fe, 0.8～0.9 Cr, 0.4～0.5 Mo, 0.3～0.5 W and 0.2 or more V move into throw out, and the throw out total amount is 3.5 or higher.
High-temperature steam turbine rotor of the present invention comprises by weight percentage by 0.25～0.35 C, 0.15 or Si still less, 0.2～0.8 Mn, 0.3～0.6 Ni, 1.6～1.9 Cr, 0.26～0.35 V, 0.6～0.9 Mo, 0.9～1.4 W, be less than 0.01 Ti, total amount is 1.3～1.4 Mo and the Fe of W/2 and surplus and the high temperature steel that unavoidable impurities is formed, wherein after tempering heat treatment, this high temperature steel is made up of the bainite single phase structure, guarantee by weight percentage 1.0 or more Fe, 0.8～0.9 Cr, 0.4～0.5 Mo, 0.3～0.5 W and 0.2 or more V move into throw out, and the throw out total amount is 3.5 or higher.
High-temperature steam turbine rotor of the present invention comprises by weight percentage by 0.25～0.35 C, 0.15 or Si still less, 0.2～0.8 Mn, 0.3～0.6 Ni, 1.6～1.9 Cr, 0.26～0.35 V, 0.6～0.9 Mo, 0.9～1.4 W, 0.001～0.007 N, total amount is 1.3～1.4 Mo and the Fe of W/2 and surplus and the high temperature steel that unavoidable impurities is formed, wherein after tempering heat treatment, high temperature steel is made up of the bainite single phase structure, guarantee by weight percentage 1.0 or more Fe, 0.8～0.9 Cr, 0.4～0.5 Mo, 0.3～0.5 W and 0.2 or more V move into throw out, the throw out total amount is 3.5 or higher.
According to above-mentioned high-temperature steam turbine rotor, comprise that the high-temperature steam turbine rotor of bainite single phase structure can form by the content range internal shaping of the one-component element described in the above.Like this, if the high-temperature behavior of can be provided in, toughness, embrittlement performance or the like aspect excellence, do not contain the amount increase that produces and will reduce the ferritic phase of the mechanical property of materials or the high-temperature steam turbine rotor of analogue greatly.Above-described component element Ti and/or N can be replaced by Fe and C.When high-temperature steam turbine rotor is in smooth operation, be exposed at high-temperature steam turbine rotor steam part near operation is equivalent to 100,000 hours postprecipitation things under top temperature total amount guarantee 2.8% or higher.The top temperature of steam is about 540～580 ℃ during smooth operation.
High-temperature steam turbine rotor is high pressure rotor, middle pressure rotor or high pressure rotor.It is with 300 ℃ or higher exhaust temperature with at the final stage outlet of the intermediate pressure section of middle pressure rotor or the high pressure rotor rotor with the steam turbine of 200 ℃ or higher exhaust temperature running in the outlet of the final stage of high pressure rotor or high pressure rotor high-pressure section.Waste vapour is introduced in the boiler or low-pressure turbine of separate configurations.
Embodiment
Embodiment of various details.
The reason of the range limited system of indivedual compositions of the alloy that uses among the present invention at first, is described.Unless otherwise mentioned, otherwise be described below in the expression composition " % " linear module refer to " weight % ".
(1) C (carbon)
C a kind ofly helps dispersion-strengthened and the inevitable element of the carbide component of the performance of guaranteeing to quench as various.If its content is lower than 0.25%, above-mentioned effect is just little.If its content surpasses 0.35%, grain coarsening that will the accelerated carbonation thing, and also sedimentary tendency also can be strengthened during ingot solidification.Therefore, determine that C content in 0.25～0.35% scope, more wishes in 0.27～0.33% scope.
(2) Si (silicon)
Si is as deoxidant element and to improve anti-steam oxidation effect be useful.But if its content height, toughness will reduce and embrittlement is quickened.Therefore, wish that its content is low as far as possible.If the content of Si surpasses 0.15%, above-mentioned favourable performance will reduce greatly.Therefore, the content of determining Si was no more than for 0.15% (not comprising 0).The content of Si preferably is no more than 0.1%.
(3) Mn (manganese)
Mn is a kind of useful element as the desulfurization element, if but its content is lower than 0.2%, its sweetening effectiveness is just not obvious, and if its add-on surpass 0.8%, its creep strength will reduce.Therefore, the content of determining Mn is in 0.2～0.8% scope, more preferably in 0.4～0.8% scope.
(4) Cr (chromium)
Cr is a kind of effective element and also is indispensable as the component that helps to strengthen the carbonitride of separating out for resistance to oxidation effect and erosion resistance.In according to high temperature steel of the present invention, Cr also is useful as improving the flexible effective element.If the content of Cr is lower than 1.6%, enter after the tempering heat treatment carbonitride Cr amount just seldom, thereby just can't guarantee the high-temperature stability of carbonitride.If the content of Cr surpasses 1.9%, anti-temper softening ability will reduce, and desirable normal temperature strength just can not guarantee, and creep strength reduces.Therefore, determine that the content of Cr is in 1.6～1.9% scope.
(5) V (vanadium)
V helps the formation of solution strengthening and meticulous carbonitride.If the content of V is 0.26% or higher, will deposit enough finer precipitates to suppress the recovery of bainite structure, if still its content surpasses 0.35%, its toughness will reduce, and the grain coarsening of carbonitride also can be quickened.Therefore, determine that the content of V is in 0.26～0.35% scope.
(6) W (tungsten)
W helps the solution strengthening and the dispersion-strengthened of bainite structure by the component that becomes carbonitride.Especially add fashionablely together as W and Mo, can significantly improve sedimentary high-temperature stability.W is along with the variation of the time of long-time heating at high temperature enters the throw out from bainite structure.Therefore, the content that is necessary to set W is 0.9% or higher to maintain the content of the W that helps long-time high solution strengthening.But if the content of W surpasses 1.4%, toughness will reduce, and will be easy to produce ferrite, and the component of large steel ingot precipitation tendency will increase.Therefore, the content of determining W is in 0.9～1.4% scope, more preferably in 0.9～1.2% scope.
(7) Mo (molybdenum)
Mo helps solution strengthening and dispersion-strengthened by the component that becomes carbonitride.Especially add fashionablely together as Mo and W, can significantly improve sedimentary high-temperature stability.Mo is along with the variation of the time of long-time heating at high temperature enters the throw out from bainite structure.Therefore, the content that is necessary to set Mo is 0.6% or higher to maintain the content of the Mo that helps long-time high solution strengthening.But if the content of Mo surpasses 0.9%, toughness will reduce, and will be easy to produce ferrite, and the component of large steel ingot precipitation tendency will increase.Therefore, the content of determining Mo is in 0.6～0.9% scope, more preferably in 0.7～0.9% scope.
(8) N (nitrogen)
N forms nitride or thereby carbonitride helps dispersion-strengthened.In addition, the N that remains in the bainite structure also helps solution strengthening, if but the content of N is lower than 0.001%, and above-mentioned effect is just not obvious.And if the content of N surpasses 0.007%, the grain coarsening of nitride or carbonitride will be quickened, and creep strength reduces.Therefore, determine that the content of N is in 0.001～0.007% scope.For the formation of carbonitride in the high temperature steel of the present invention, can replace N by the content that in the scope of C content, increases C.Fe also can be used to replace N.
(9) Ti (titanium)
Ti is useful as deoxidant element.If the content of Ti is lower than 0.01%, it just can bring into play desoxydatoin, and remaining Ti forms sosoloid.But if the content of Ti surpasses 0.01%, the generation of the Ti carbonitride of non-solid solution body alligatoring will increase, thereby causes the reduction of flexible reduction or otch.Therefore, the content of determining Ti was lower than for 0.01% (not comprising 0).Ti makes that the amount of O (oxygen) reduces by desoxydatoin in the steel ingot comprising in above-mentioned content, and also can prevent the formation of oxide compound in the steel ingot manufacturing.Ti can replace by the content that increases C in the scope of C content.And Fe also can be used to replace Ti.
(10) Ni (nickel)
Ni improves quenching performance and toughness and has the effect that ferrite produces that suppresses.When the content of Ni is 0.35 or can observes this effect when higher.But if the content of Ni surpasses 0.6%, creep strength will reduce.Therefore, determine that the content of Ni is in 0.3～0.6% scope.
It is desirable reducing the accidental impurity of infiltrating when adding above-described component and main ingredient Fe as far as possible.Unavoidable impurities comprises P (phosphorus), S (sulphur), Cu (copper), Al (aluminium), As (arsenic), Sn (tin), Sb (antimony) and O (oxygen) in the high temperature steel of the present invention.These impurity can be under the high temperature at high temperature steel and cause embrittlement in the long-time heating.With regard to the element of those unavoidable impurities, it is desirable making their content reduce to zero as much as possible, particularly is lower than 0.015% P, is lower than 0.005% S, is lower than 0.1% Cu, is lower than 0.01% Al, is lower than 0.005% As, 0.005% Sn, the oxygen that is lower than 0.005% Sb and is lower than 20ppm.
Next, the total amount of describing Mo and W/2 is limited in 1.3～1.4 reason.
In the high temperature steel of the present invention, each has W and Mo as the effect described in top (6) and (7).When they add fashionablely together, the raising of creep strength can be better than when they add fashionable raising respectively, yet when making large steel ingot, the precipitation of light element component tendency can increase greatly.Therefore be necessary to limit amount that W and Mo add together to bring into play desirable creep strength and to avoid precipitation.For the consideration of so doing, wish to use an index (total amount of Mo and W/2 (weight %)) that is called the Mo equivalence value usually.For high temperature steel of the present invention, when the Mo equivalence value was lower than 1.3, creep strength reduced, if the Mo equivalence value surpasses 1.4, the precipitation of component just becomes quite big in the large steel ingot manufacturing.Therefore, determine that Mo equivalence value (total amount of Mo and W/2 (weight %)) is 1.3～1.4.
Then, what is described as wherein after the high temperature steel tempering heat treatment of element add-on in above-mentioned scope by weight percentage 1.0 or more Fe, 0.8～0.9 Cr, 0.4～0.5 Mo, 0.3～0.5 W and 0.2 or more V is included in the throw out and sedimentary total amount is guaranteed 3.5 or higher reason.
High temperature steel of the present invention strengthens by the solution strengthening and the separating out of carbonitride of bainite structure.Carbonitride is separated out wittingly by tempering heat treatment, and the throw out in the high temperature steel of the present invention is M, VC, R type, M, RC type, M, four types on QC type and MC type.M refers to metallic element.M, VC, R type and M, the M in the RC type mainly are Fe and Cr, and may comprise Mo, W or the like in addition.M, the M in the QC type mainly are Mo and W, and may comprise V in addition.M in the MC type mainly is V, and may comprise Mo and W in addition.
What will be described as below above-mentioned Fe, Cr, Mo, W and V will be limited in reason in the compositional range separately.Unless otherwise mentioned, the linear module of " % " of expression composition refers to " weight % " otherwise in describing below.
Measure and differentiate sedimentary amount as follows.Specimen is placed in the mixing liquid of methyl alcohol, methyl ethyl diketone and Tetramethylammonium chloride, by the electrolytic dissolution bainite structure.After the filtration, with the washing of resulting resistates and weigh.Use is by the determined value of ratio of weight before and after the dissolving.In addition, the resistates of recovery is determined sedimentary kind by x-ray analysis or similar analysis.
(11) Fe (iron)
Fe in the throw out is M, VC, and R type and M, the sedimentary main component element of RC type, it helps dispersion-strengthened.If it is the Fe amount that enters after the tempering heat treatment in the throw out is lower than 1.0%, insufficient thereby the little dispersion-strengthened action of so sedimentary amount carries out.In order to bring into play creep strength, after tempering heat treatment as M, it is effective using time dependent conversion after the RC type precipitate, but, if the amount of movement of Fe is lower than 1.0%, M, the sedimentary precipitation capacity of RC type is little, so can not expect to obtain by this method the increase of creep strength.Therefore, after the tempering heat treatment in the throw out content of Fe be defined as 1.0% or higher.
(12) Cr (chromium)
Cr in the throw out is M, VC, and R type and M, the sedimentary main component element of RC type, it helps dispersion-strengthened.Cr replaces the part Fe in the throw out, so it also has the effect that improves throw out stability.If the Cr amount that enters after the tempering heat treatment in the throw out is lower than 0.8%, so sedimentary amount is little, and is insufficient thereby dispersion-strengthened action carries out.And if the Cr amount that enters after the tempering heat treatment in the throw out surpasses 0.9%, during tempering heat treatment, will cause Fe, the sedimentary disappearance of RC type, thereby the time lag effect described in (11) above just can not bringing into play.Therefore, after the tempering heat treatment in the throw out content of Cr determine in the scope 0.8～0.9%.
(13) W (tungsten)
W in the throw out is M, the sedimentary main component element of QC type, and it helps dispersion-strengthened.W replaces M, VC, and R type, M, a RC type and the sedimentary part of MC type, so it has improved sedimentary high-temperature stability greatly.If the W amount that enters after the tempering heat treatment in the throw out is lower than 0.3%, sedimentary stability is just low, just can not bring into play desirable creep strength.And if the W amount that enters after the tempering heat treatment in the throw out surpasses 0.5%, the solid solution capacity of W will reduce in the bainite structure, thereby the solution strengthening amount under the high temperature reduces.Therefore, the content of the W in tempering heat treatment postprecipitation thing is determined in the scope 0.3～0.5%.
(14) Mo (molybdenum)
Mo in the throw out is M, the sedimentary main ingredient element of QC type, and it helps dispersion-strengthened.Mo replaces M, VC, and R type, M, a RC type and the sedimentary part of MC type, thus improved sedimentary high-temperature stability greatly.If the Mo amount that enters after the tempering heat treatment in the throw out is lower than 0.4%, sedimentary stability is just low, thereby can not bring into play desirable creep strength.And if the Mo amount that enters after the tempering heat treatment in the throw out surpasses 0.5%, the solid solution capacity of the Mo in the bainite structure will reduce, thereby the solution strengthening amount under the high temperature reduces.Therefore, after the tempering heat treatment in the throw out content of Mo determine in the scope 0.4～0.5%.
(15) V (vanadium)
V in the throw out is the sedimentary main component element of meticulous MC type, and it helps dispersion-strengthened.V replaces M, VC, and R type, M, RC type and M, the sedimentary part of QC type, thus improved sedimentary high-temperature stability greatly.If the V amount that enters after the tempering heat treatment in the throw out is lower than 0.2%, the sedimentary precipitation capacity of MC type will reduce, thus other sedimentary stable step-down.Therefore, the content of the V in the throw out is defined as 0.2% or more after tempering heat treatment.
For the sedimentary meticulous and uniform dispersion of mainly being made up of by tempering heat treatment five kinds of elements and C, N or the like of above-mentioned (11)～(15), requiring sedimentary total amount is 3.5% or more.If total amount is lower than 3.5%, strength characteristic and sedimentary high-temperature stability will reduce described in above-mentioned (11)～(15).Therefore, the total amount of tempering heat treatment postprecipitation thing is defined as 3.5% or more.
Next, what is described as after the tempering heat treatment of the formed high-temperature steam turbine rotor of forming by the component in the scope of above-mentioned (1)～(10) of high temperature steel, even be equivalent to 100 in running, after 000 hour, near the part of the steam when being exposed to smooth operation under the top temperature throw out total amount is preferably guaranteed the sedimentary total amount (3.5%) of above-mentioned (11)～(15) 2.8% or more reason under situation about reducing to some extent after the tempering heat treatment.
The high temperature steel that is configured as high-temperature steam turbine rotor of the present invention is different from common high temperature steel, the solid solution capacity of its carbonitride between on-stream period and precipitation capacity time to time change, thus cause the performance of the high-temperature behavior of giving prominence to.The Mo and the W that are in supersaturation solution state in the high temperature steel mainly enter M in time, in QC type throw out and the MC type throw out, to improve their high-temperature stability, contain M as the main ingredient element of Fe, RC type throw out changes in time than working as and contains as the more stable M of main ingredient element Cr, VC, R type throw out is to keep creep strength.Particularly, the latter comprises Fe by tempering heat treatment and a large amount of sedimentary M, and the dissolving in the RC type throw out is so that the throw out total amount after sedimentary total amount and the tempering heat treatment is compared minimizing.Remaining M, RC type throw out have the effect that keeps creep strength, still, if sedimentary total amount is lower than 2.8%, M, RC type throw out will be eliminated fully, thus dispersion-strengthened action will reduce rapidly.Therefore, be equivalent to 100,000 hours postprecipitation thing total amounts in running and be confirmed as 2.8% or more.
The throw out that is deposited in the high temperature steel that is configured as high-temperature steam turbine rotor is being different aspect the precipitation capacity that depends on their types, and their precipitation capacity is variable in time, this depends on the running of high-temperature steam turbine rotor, but does not have the throw out deposition of novel type when running.The top temperature of steam is in 540～580 ℃ scope during the smooth operation.
Next, the particle diameter that is described as what original austenite is preferably 100 μ m or littler reason on average.
The original austenite particle diameter has bigger influence to independent mechanical property.If it surpasses 100 μ m, ductility will reduce, and the crystal boundary place is easy to produce the crack, and notch creep intensity and toughness reduce.Therefore, the particle diameter of original austenite is defined as 100 μ m or littler on average.
Particle diameter is to depend on the Heating temperature when quenching and finally determine.For high temperature steel of the present invention, 980～1030 ℃ Heating temperature is desirable.If Heating temperature is lower than 980 ℃, just can not obtains sufficient quenching effect, and can not bring into play desirable mechanical property.And if Heating temperature surpasses 1030 ℃, the particle alligatoring that will obviously become.Performance obviously reduces with above-mentioned grain coarsening.
High temperature steel of the present invention and high-temperature steam turbine rotor comprise the element in the stated limit of being in of above-mentioned (1)～(10), and the Mo equivalence value is in specified scope, and the original austenite particle diameter is 100 μ m or littler on average.And the element described in above-mentioned (11) and (12) is included within the throw out with specified scope.After running was equivalent to 100,000 hours, near the part when high-temperature steam turbine rotor is exposed to smooth operation under the steam of top temperature, sedimentary total amount can be secured at specified value or more, and can correspondingly bring into play desirable mechanical property.
As the high temperature steel that comprises ferrite former such as Cr, Mo, W, V or the like of the present invention, in metal construction, may depend on the add-on of individual element and produce ferrite.These elements concentrate in the ferrite of low alloy steel, thereby the effect of above-mentioned element can not be given full play to.Therefore, determine that high temperature steel of the present invention has the additional range of single interpolation element ((1)～(10)) so that have the bainite phase structure.
Ferritic phase can depend on Heating temperature when making or the cooling conditions after the heating and produce.Particularly repeat the place that heating and cooling and turbine rotor have big scantling in manufacturing processed, ferritic phase depends on the speed of cooling when for example quenching and produces.In other words, ferritic phase has the feature that produces when being exposed to the fixed time in the specified for temperature ranges.For example, if the speed of cooling when quenching is low, it will pass at cooling stages and produce the zone.As a result, the structure that has ferritic phase that obtains in bainite structure, producing, thus performance reduces.
Even when carbonitride deposits in ferrite, to compare with the bainite phase structure, performance also can reduce, and constituent concentration and structure become inhomogeneous inevitably.Therefore, the generation zone during for fear of quenching, in the manufacturing of high temperature steel, the acquisition of the adjusting of speed of cooling and bainite phase structure is noticeable.
Even now still can provide contain according to composition range of the present invention, have the bainite single phase structure, have under the high temperature good mechanical property and need not to limit the high temperature steel and the high-temperature steam turbine rotor of speed of cooling.In addition,, in the high-temperature steam environment, can carry out stable running, and also be good aspect economical efficiency according to high temperature steel of the present invention and high-temperature steam turbine rotor.
The various details embodiment.
(first embodiment)
What will describe is the performance that has excellence according to the high temperature steel of one embodiment of the invention.By dissolving about 30 kilograms of material, casting, forge hot ingot castings with chemical ingredients scope of the present invention, annealing, standardize and sample steel in first embodiment is made in quenching and tempering.Quench in 980～1030 ℃ on ingot casting in normalization back, so that the speed of cooling of ingot casting center is approximately 20～80 ℃/h.
Table 1 has been listed the chemical ingredients of the sample steel of making.Among the sample steel shown in the table 1, die P1～die P14 is the high temperature steel that contains according to the composition of the scope of the invention.And die C1～die C6 contains the high temperature steel that is not according to the chemical ingredients of the scope of the invention, is comparative example.Table 1 has also been listed the residual volume of the oxygen of each die.Numerical value in the table 1 by weight percentage.
As shown in table 1, the residual volume that comprises oxygen in the sample steel of Ti mostly is 10ppm most.This value is lower than the residual volume of oxygen in the sample steel that does not contain Ti, and this shows that the desoxydatoin that adds by Ti operates effectively.But die C2 has desoxydatoin produces the Ti carbonitride that is in the non-solid solution attitude.
Die shown in the adjustment sheet 1 makes it have 0.02% yielding stress of about 660～690MPa under the normal temperature that is suitable for turbine rotor as shown in table 2.
For each die, preparation has the notched specimen according to the pendulum impact test of JIS Z2202 of being used for of 2mm thickness and v-notch, and carries out pendulum impact test with these samples.Test result is as shown in table 2.Table 2 has also been listed the measuring result of repture test rupture time under 600 ℃ and 196MPa condition.
Die P1～the P14 that is in the embodiment in the chemical ingredients scope of the present invention has 20 ℃ of shock absorption energy of 50～55J down.And the die C1～C6 of comparative example has 20 ℃ of down shock absorption energy of maximum 40J, and the shock absorption energy is low than in the embodiment generally.
For each steel of the die P1～P14 of embodiment, the rupture time in the repture test of carrying out under 600 ℃ and 196MPa condition is the shortest to be about 1850 hours.And the creep fracture time of the die C1～C6 of comparative example is 800～1530 hours.
In the die of comparative example, have die C1, the die C3 of long relatively rupture time and the shock absorption energy that die C5 has each the die shock absorption energy that is starkly lower than embodiment under 20 ℃.When Mo equivalence value (total amount of Mo and W/2 (weight %)) be lower than as die C4 had 1.3 and when the Mo equivalence value surpass as die C5 had 1.4 the time, creep fracture time is obviously very short.In addition, though the Mo equivalence value in 1.3～1.4 scope, if the add-on of other element not in chemical ingredients scope of the present invention, creep fracture time is also short and the shock absorption energy is also low.
Can find from above, under adjusting to same normal temperature during 0.02% yielding stress, the high temperature steel of embodiment and the amount that contains the addition element to some extent not high temperature steel of the comparative example within composition range of the present invention are compared and are had fabulous shock absorption energy and creep fracture time value.And what can see equally is that the adding of Ti has reduced the amount of residual oxygen in the steel ingot.
Table 1
| Die | C | Si | Mn | Ni | Cr | V | W | Mo | Ti | N | O(ppm) | Fe | Mo+W/2 | |
| Embodiment | P1 | 0.27 | 0.05 | 0.31 | 0.35 | 1.78 | 0.28 | 1.16 | 0.75 | 0.007 | 0.006 | 9 | Surplus | 1.330 |
| P2 | 0.26 | 0.06 | 0.29 | 0.35 | 1.62 | 0.29 | 1.38 | 0.66 | 0.002 | 0.006 | 8 | Surplus | 1.350 | |
| P3 | 0.27 | 0.05 | 0.33 | 0.38 | 1.85 | 0.35 | 0.91 | 0.86 | 0.008 | 0.005 | 9 | Surplus | 1.315 | |
| P4 | 0.31 | 0.09 | 0.59 | 0.42 | 1.72 | 0.31 | 1.01 | 0.88 | 0.003 | 0.005 | 9 | Surplus | 1.385 | |
| P5 | 0.32 | 0.12 | 0.55 | 0.32 | 1.67 | 0.30 | 1.28 | 0.73 | 0.002 | 0.005 | 10 | Surplus | 1.370 | |
| P6 | 0.31 | 0.05 | 0.61 | 0.31 | 1.88 | 0.34 | 0.97 | 0.89 | 0.003 | - | 8 | Surplus | 1.375 | |
| P7 | 0.34 | 0.04 | 0.78 | 0.48 | 1.82 | 0.34 | 1.37 | 0.64 | 0.001 | - | 7 | Surplus | 1.325 | |
| P8 | 0.31 | 0.07 | 0.72 | 0.54 | 1.70 | 0.31 | 1.22 | 0.71 | 0.002 | 0.004 | 9 | Surplus | 1.320 | |
| P9 | 0.30 | 0.05 | 0.21 | 0.36 | 1.75 | 0.26 | 1.21 | 0.73 | 0.005 | 0.006 | 10 | Surplus | 1.335 | |
| P10 | 0.31 | 0.06 | 0.55 | 0.52 | 1.85 | 0.35 | 1.36 | 0.63 | - | 0.007 | 15 | Surplus | 1.310 | |
| P11 | 0.29 | 0.06 | 0.59 | 0.37 | 1.72 | 0.32 | 1.39 | 0.62 | - | 0.003 | 14 | Surplus | 1.315 | |
| P12 | 0.29 | 0.07 | 0.60 | 0.31 | 1.61 | 0.34 | 1.09 | 0.82 | - | 0.005 | 16 | Surplus | 1.365 | |
| P13 | 0.33 | 0.09 | 0.45 | 0.42 | 1.74 | 0.29 | 0.92 | 0.85 | - | - | 12 | Surplus | 1.310 | |
| P14 | 0.33 | 0.06 | 0.52 | 0.39 | 1.65 | 0.27 | 1.31 | 0.74 | - | - | 14 | Surplus | 1.395 | |
| CE * | C1 | 0.24 | 0.05 | 0.68 | 0.44 | 1.83 | 0.27 | 0.67 | 1.02 | - | 0.004 | 15 | Surplus | 1.355 |
| C2 | 0.28 | 0.17 | 0.51 | 0.53 | 1.79 | 0.28 | 1.52 | 0.55 | 0.009 | - | 9 | Surplus | 1.310 | |
| C3 | 0.30 | 0.05 | 0.59 | 0.35 | 1.15 | 0.28 | - | 1.33 | - | 0.003 | 16 | Surplus | 1.330 | |
| C4 | 0.05 | 0.19 | 0.49 | 0.02 | 2.23 | 0.23 | 1.58 | 0.12 | - | 0.008 | 14 | Surplus | 0.910 | |
| C5 | 0.25 | 0.07 | 0.82 | 0.84 | 1.25 | 0.25 | 0.42 | 1.25 | - | - | 13 | Surplus | 1.460 | |
| C6 | 0.36 | 0.05 | 0.17 | 0.25 | 1.85 | 0.33 | 1.36 | 0.65 | - | 0.002 | 16 | Surplus | 1.330 |
*CE: comparative example
Table 2
| Die | 0.02% yielding stress (MPa) under the room temperature | Creep fracture time under the 600 ℃-196Mpa (h) | 20 ℃ absorption energy (J) | |
| Embodiment | P1 | 675 | 2178 | 55 |
| P2 | 670 | 1942 | 52 | |
| P3 | 690 | 2054 | 54 | |
| P4 | 665 | 1905 | 53 | |
| P5 | 670 | 2008 | 50 | |
| P6 | 685 | 2265 | 50 | |
| P7 | 670 | 1895 | 55 | |
| P8 | 673 | 1854 | 50 | |
| P9 | 669 | 2058 | 50 | |
| P10 | 680 | 1980 | 52 | |
| P11 | 668 | 2057 | 50 | |
| P12 | 670 | 2237 | 50 | |
| P13 | 690 | 1878 | 52 | |
| P14 | 680 | 1968 | 50 | |
| Comparative example | C1 | 664 | 1527 | 12 |
| C2 | 674 | 927 | 18 | |
| C3 | 665 | 1347 | 12 | |
| C4 | 658 | 812 | 40 | |
| C5 | 660 | 1280 | 25 | |
| C6 | 668 | 983 | 31 |
(second embodiment)
What will describe is when the high temperature steel that contains chemical ingredients scope of the present invention is carried out tempering heat treatment, wishes it is adjusted to the state of guaranteeing to specify precipitation capacity.
In second embodiment, the die P1 shown in the table 1, die P6, die P11 and die P14 from 990 ℃ of quenchings, so that be approximately 20～80 ℃/h in the speed of cooling of sample steel center, and are carried out tempering heat treatment under 630～730 ℃.
Table 3 has been listed after the tempering heat treatment of sample steel in the content (weight %) and the sedimentary total amount (weight %) that are contained in Fe, Cr, Mo, W and V in the middle of the sedimentary element.Table 3 has also been listed the measuring result of carrying out the rupture time of repture test under 600 ℃ and the 196MPa condition on the sample steel.
From the measuring result shown in the table 3 as can be seen, within the content that is contained in sedimentary individual element after the tempering heat treatment of each die shown in comparative example be not contained in the above-mentioned scope of the constituent content in the throw out of the present invention and when throw out total amount during less than the scope (3.5 weight % or more) of throw out total amount of the present invention, it is quite short that creep fracture time becomes.
Simultaneously, as can be seen, the high temperature steel (embodiment) that reaches the content that is contained in the sedimentary element of the present invention and have a throw out total amount that is not less than throw out total amount of the present invention (3.5 weight % or more) shows excellent creep fracture performance.As the die P1 from table 2, die P6, die P11 and die P14 the result supposed, in each die, the high temperature steel shown in the embodiment not only can be guaranteed creep fracture performance and can guarantee enough shock absorption energy.
Table 3
| Die | Content (Wt%) in the tempering heat treatment postprecipitation thing | Sedimentary total amount (Wt%) | 600 ℃-196 MPa creep fracture times (h) | |||||
| Fe | Cr | Mo | W | V | ||||
| P1 | E | 1.27 | 0.85 | 0.46 | 0.36 | 0.26 | 3.77 | 2065 |
| E | 1.54 | 0.85 | 0.42 | 0.42 | 0.26 | 3.89 | 2178 | |
| CE | 0.95 | 0.83 | 0.34 | 0.28 | 0.24 | 3.34 | 1684 | |
| P6 | E | 1.67 | 0.86 | 0.45 | 0.41 | 0.29 | 4.08 | 2084 |
| E | 1.90 | 0.86 | 0.47 | 0.47 | 0.29 | 4.16 | 2265 | |
| CE | 0.92 | 0.77 | 0.37 | 0.28 | 0.23 | 3.42 | 1551 | |
| P11 | E | 1.85 | 0.82 | 0.44 | 0.45 | 0.27 | 4.05 | 2057 |
| CE | 1.43 | 0.92 | 0.52 | 0.53 | 0.27 | 3.96 | 1478 | |
| P14 | E | 1.95 | 0.82 | 0.43 | 0.39 | 0.25 | 3.65 | 1968 |
| E | 1.29 | 0.84 | 0.55 | 0.51 | 0.24 | 4.23 | 1069 | |
| CE | 0.63 | 0.57 | 0.24 | 0.21 | 0.18 | 2.05 | 976 | |
E=embodiment; The CE=comparative example
(the 3rd embodiment)
What will describe is that high temperature steel in will being in chemical ingredients scope of the present invention is when carrying out tempering heat treatment, make them adjust to the state of guaranteeing to specify precipitation capacity, and hope will be exposed near the sedimentary total amount of part of high-temperature steam under the assigned temperature and guarantee at 2.8 weight % or higher after operation is equivalent to 100,000 hours.
In the 3rd embodiment, tempering heat treatment postprecipitation thing total amount shown in the table 1 is satisfied the content range be contained in the sedimentary element of the present invention, and the high temperature steel that the throw out total amount is not less than sedimentary total amount of the present invention (3.5 weight % or higher) or higher die P2, die P7, die P10 and die P13 is determined as the sample steel.And, the sample steel heated under the temperature of 550～600 ℃ of scopes be equivalent to 100,000 hours.
Table 4 has been listed the measuring result that tempering heat treatment postprecipitation thing total amount and heating are equivalent to 100,000 hours postprecipitation thing total amounts, and the measuring result of the rupture time that is obtained by repture test under 600 ℃ and 196MPa condition.
From the measuring result shown in the table 4 as can be seen, when the total amount of heating postprecipitation thing surpasses 2.8 weight % (embodiment hurdle), creep fracture time is 1500 hours or more, with respect to the creep fracture time of the P1～P14 of die shown in the table 2 guarantee rupture time at least 80% or more.And when the total amount of heating postprecipitation thing was lower than 2.8% (comparative example hurdle), creep fracture time was about 700～825 hours, and rupture time just is about 40% of the P1 of die shown in the table 2～P14 creep fracture time.
As can be seen from the above, when the high temperature steel in will being in chemical ingredients scope of the present invention carries out tempering heat treatment, (11)～(12) element described in is included in the throw out with specified scope, and when heating under 550～600 ℃ high temperature for example is equivalent to 100, if 000 hour and like this after sedimentary total amount become 2.8 weight % or when higher, can access and compare quite long creep fracture time with the comparative example that does not reach that throw out total amount.
Table 4
| Die | The total amount (Wt%) of tempering heat treatment postprecipitation thing | Embodiment | Comparative example | ||
| The total amount (Wt%) of heating postprecipitation thing | 600 ℃-196MPa creep fracture time (h) | The total amount (Wt%) of heating postprecipitation thing | 600 ℃-196MPa creep fracture time (h) | ||
| P2 | 3.87 | 2.93 | 1624 | 2.76 | 825 |
| P7 | 3.71 | 2.86 | 1520 | 2.61 | 811 |
| P10 | 4.02 | 3.22 | 1648 | 2.35 | 703 |
| P13 | 4.18 | 3.71 | 1585 | 2.73 | 796 |
(the 4th embodiment)
What will describe is that the high temperature steel that is in the chemical ingredients scope of the present invention is suitable for having little constituent concentration precipitation and the manufacturing of steel ingot uniformly.
According to the 4th embodiment, suppose 60 tons of manufacturings or the steel ingot that more has the chemical ingredients of die P6 as shown in table 1, die P12, die C2 and die C6, and sedimentary tendency is carried out numerical simulation.
According to numerical simulation, analyze by use have be about 1.5 by casting the time mould diameter divided by the ingot casting of the mould manufacturing of the resulting value of height of mould at the concentration of component of centre portions on short transverse that is solidifying the back ingot casting.
Table 5 has been listed the analytical results that is configured as the concentration of component of the lightest element C in the above-mentioned die and the heaviest element W at those.Value in the table 5 is that concentration of component by molten metal is divided by the resulting value of the concentration of component of steel ingot various piece.And the distance from steel ingot bottom 100% is meant the top of steel ingot.
From the analytical results shown in the table 5 as can be seen, in the scope of concentration ratio 0.93～1.15 of light element C in die P6 and die P12, and the concentration ratio of heavy element W in die P6 and die P12 is about 1.0.Simultaneously, as can be seen, the concentration ratio of C in die C2 and die C6 uprises and sizable component precipitation takes place towards the direction of ingot butt.
From The above results as can be seen, chemical ingredients scope of the present invention is suitable for having little concentration of component precipitation and the manufacturing of steel ingot uniformly.
Table 5
| Die | Element | Distance from the steel ingot bottom | ||||
| 5％ | 30％ | 50％ | 80％ | 100％ | ||
| P6 | C | 0.94 | 0.97 | 1.00 | 1.00 | 1.12 |
| W | 1.03 | 1.02 | 1.02 | 1.02 | 1.03 | |
| P12 | C | 0.93 | 0.97 | 1.03 | 1.09 | 1.15 |
| W | 1.02 | 1.04 | 1.00 | 1.03 | 1.04 | |
| C2 | C | 0.93 | 0.98 | 1.03 | 1.26 | 1.36 |
| W | 1.07 | 1.04 | 1.03 | 1.03 | 1.04 | |
| C6 | C | 0.91 | 0.94 | 1.15 | 1.21 | 1.35 |
| W | 1.08 | 1.08 | 1.07 | 1.05 | 1.05 | |
(the 5th embodiment)
What will describe is that the original austenite particle diameter of wishing to have the high temperature steel of chemical ingredients scope of the present invention why is adjusted on average 100 μ m or still less.
According to the 5th embodiment, use die P3, die P7, die P12 and the die P13 shown in the table 1 as the sample steel.By the particle diameter of hot-work adjustment sample steel, then, they are adjusted to 0.02% yielding stress of about 660～690MPa under the normal temperature that is suitable for turbine rotor.
Particle diameter by the testing method measure sample steel of description among the JIS G 0551.And, the relative reduction in area under measuring 300 ℃ according to the tensile test method described in the JIS Z 2241.Whether in addition, measure notch creep breaking tenacity that 300 ℃ of following repture tests obtain compares with lubricant and improves or reduce.
Table 6 has been listed the result of above-mentioned measurement.
From the measuring result shown in the table 6 as can be seen, if the original austenite particle diameter is no more than 100 μ m (embodiment), just can bring into play stretching relative reduction in area and notch strength 50% or more, but, if the original austenite particle diameter surpasses 100 μ m (comparative example), the stretching relative reduction in area will sharply reduce, and breach also can be weakened.
As can be seen from the above, You Yi stretch characteristic and creep fracture performance can be by adjusting to specified sedimentation state and particle diameter adjusted to 100 μ m or littler the performance at the high temperature steel in the chemical ingredients scope of the present invention.
Table 6
| Die | Particle diameter (μ m) | Stretching relative reduction in area under 300 ℃ | Notch creep | |
| P3 | E | 60 | 55 | Breach is strengthened |
| E | 95 | 50 | Breach is strengthened | |
| CE | 110 | 28 | The breach reduction | |
| P7 | E | 55 | 57 | Breach is strengthened |
| E | 80 | 52 | Breach is strengthened | |
| CE | 110 | 28 | The breach reduction | |
| P12 | E | 70 | 57 | Breach is strengthened |
| CE | 105 | 26 | The breach reduction | |
| P13 | E | 85 | 55 | Breach is strengthened |
| CE | 120 | 25 | The breach reduction |
E=Embodiment C E=comparative example
The present invention is not limited to above-mentioned embodiment, can carry out different modifications and variations in technical scope of the present invention.The embodiment of revising or changing is also included within the technical scope of the present invention equally.
Claims (24)
1. high temperature steel, it is by weight percentage by 0.25～0.35 C, 0.15 or Si still less, 0.2～0.8 Mn, 0.3～0.6 Ni, 1.6～1.9 Cr, 0.26～0.35 V, 0.6～0.9 Mo, 0.9～1.4 W, be lower than 0.01 Ti, 0.001～0.007 N, total amount is that the Fe and the unavoidable impurities of 1.3～1.4 Mo and W/2 and surplus formed, wherein after tempering heat treatment, this high temperature steel is made up of the bainite single phase structure, guarantee by weight percentage 1.0 or more Fe, 0.8～0.9 Cr, 0.4～0.5 Mo, 0.3～0.5 W and 0.2 or more V move into throw out, and the throw out total amount is 3.5 or higher.
2. according to the high temperature steel of claim 1, wherein Ti and/or N are replaced by Fe and C.
3. according to the high temperature steel of claim 1 or 2, wherein high temperature steel has original austenite particle diameter average out to 100 μ m or littler tempered bainite single phase structure, even and M, RC type throw out, M, VC, R type throw out, M, QC type throw out and MC type throw out deposit in the bainite single phase structure and are exposed under the high-temperature steam of assigned temperature and be equivalent to 100,000 hour, the throw out type did not change yet.
4. high temperature steel, it is by weight percentage by 0.25～0.35 C, 0.15 or Si still less, 0.2～0.8 Mn, 0.3～0.6 Ni, 1.6～1.9 Cr, 0.26～0.35 V, 0.6～0.9 Mo, 0.9～1.4 W, be lower than 0.01 Ti, total amount is that the Fe and the unavoidable impurities of 1.3～1.4 Mo and W/2 and surplus formed, wherein after tempering heat treatment, this high temperature steel is made up of the bainite single phase structure, guarantee by weight percentage 1.0 or more Fe, 0.8～0.9 Cr, 0.4～0.5 Mo, 0.3～0.5 W and 0.2 or more V move into throw out, and the throw out total amount is 3.5 or higher.
5. according to the high temperature steel of claim 4, wherein Ti and/or N are replaced by Fe and C.
6. according to the high temperature steel of claim 4 or 5, wherein this high temperature steel has original austenite particle diameter average out to 100 μ m or littler tempered bainite single phase structure, even and M, RC type throw out, M, VC, R type throw out, M, QC type throw out and MC type throw out deposit in the bainite single phase structure and are exposed under the high-temperature steam of assigned temperature and be equivalent to 100,000 hour, the throw out type did not change yet.
7. high temperature steel, it is by weight percentage by 0.25～0.35 C, 0.15 or Si still less, 0.2～0.8 Mn, 0.3～0.6 Ni, 1.6～1.9 Cr, 0.26～0.35 V, 0.6～0.9 Mo, 0.9～1.4 W, 0.001～0.007 N, total amount is that the Fe and the unavoidable impurities of 1.3～1.4 Mo and W/2 and surplus formed, wherein after tempering heat treatment, this high temperature steel is made up of the bainite single phase structure, guarantee by weight percentage 1.0 or more Fe, 0.8～0.9 Cr, 0.4～0.5 Mo, 0.3～0.5 W and 0.2 or more V move into throw out, and the throw out total amount is 3.5 or higher.
8. according to the high temperature steel of claim 7, wherein Ti and/or N are replaced by Fe and C.
9. according to the high temperature steel of claim 7 or 8, wherein this high temperature steel has original austenite particle diameter average out to 100 μ m or littler tempered bainite single phase structure, even and M, RC type throw out, M, VC, R type throw out, M, QC type throw out and MC type throw out deposit in the bainite single phase structure and are exposed under the high-temperature steam of assigned temperature and be equivalent to 100,000 hour, the throw out type did not change yet.
10. heat treating method that is used for high temperature steel, it comprises: will be by weight percentage by 0.25～0.35 C, 0.15 or Si still less, 0.2～0.8 Mn, 0.3～0.6 Ni, 1.6～1.9 Cr, 0.26～0.35 V, 0.6～0.9 Mo, 0.9～1.4 W, be less than 0.01 Ti, 0.001～0.007 N, total amount is that the Fe of 1.3～1.4 Mo and W/2 and surplus and steel ingot that unavoidable impurities is formed are heated to 980～1030 ℃, cooling is carried out temper then so that the speed of cooling of steel ingot centre portions becomes at least 20 ℃/h or higher.
11. heat treating method that is used for high temperature steel, comprise: will be by weight percentage by 0.25～0.35 C, 0.15 or still less Si, 0.2～0.8 Mn, 0.3～0.6 Ni, 1.6～1.9 Cr, 0.26～0.35 V, 0.6～0.9 Mo, 0.9～1.4 W, to be less than 0.01 Ti, total amount be that 1.3～1.4 Mo and the Fe of W/2 and surplus and the steel ingot that unavoidable impurities is formed are heated to 980～1030 ℃, cooling is carried out temper then so that the speed of cooling of steel ingot centre portions becomes at least 20 ℃/h or higher.
12. heat treating method that is used for high temperature steel, it comprises: will be by weight percentage by 0.25～0.35 C, 0.15 or still less Si, 0.2～0.8 Mn, 0.3～0.6 Ni, 1.6～1.9 Cr, 0.26～0.35 V, 0.6～0.9 Mo, 0.9～1.4 W, 0.001～0.007 N, total amount be that 1.3～1.4 Mo and the Fe of W/2 and surplus and the steel ingot that unavoidable impurities is formed are heated to 980～1030 ℃, cooling is carried out temper then so that the speed of cooling of steel ingot centre portions becomes at least 20 ℃/h or more.
13. high-temperature steam turbine rotor that comprises high temperature steel, described high temperature steel is by weight percentage by 0.25～0.35 C, 0.15 or Si still less, 0.2～0.8 Mn, 0.3～0.6 Ni, 1.6～1.9 Cr, 0.26～0.35 V, 0.6～0.9 Mo, 0.9～1.4 W, be less than 0.01 Ti, 0.001～0.007 N, total amount is that the Fe and the unavoidable impurities of 1.3～1.4 Mo and W/2 and surplus formed, wherein after tempering heat treatment, this high temperature steel is made up of the bainite single phase structure, guarantee by weight percentage 1.0 or more Fe, 0.8～0.9 Cr, 0.4～0.5 Mo, 0.3～0.5 W and 0.2 or more V move into throw out, and the throw out total amount is 3.5 or higher.
14. according to the high-temperature steam turbine rotor of claim 13, wherein when smooth operation, be exposed to top temperature steam high-temperature steam turbine rotor part near running be equivalent to guarantee after 100,000 hours that the throw out total amount is 2.8% or more.
15. high-temperature steam turbine rotor according to claim 13 and 14, wherein this high-temperature steam turbine rotor has original austenite particle diameter average out to 100 μ m or littler tempered bainite single phase structure, even and M, RC type throw out, M, VC, R type throw out, M, QC type throw out and MC type throw out deposit in the bainite single phase structure and are exposed under the top temperature steam when smooth operation and be equivalent to 100,000 hour, the throw out type did not change yet.
16. according to the high-temperature steam turbine rotor of claim 13, wherein Ti and/or N are replaced by Fe and C.
17. high-temperature steam turbine rotor that comprises high temperature steel, described high temperature steel is by weight percentage by 0.25～0.35 C, 0.15 or Si still less, 0.2～0.8 Mn, 0.3～0.6 Ni, 1.6～1.9 Cr, 0.26～0.35 V, 0.6～0.9 Mo, 0.9～1.4 W, be less than 0.01 Ti, total amount is that the Fe and the unavoidable impurities of 1.3～1.4 Mo and W/2 and surplus formed, wherein after tempering heat treatment, this high temperature steel is made up of the bainite single phase structure, guarantee by weight percentage 1.0 or more Fe, 0.8～0.9 Cr, 0.4～0.5 Mo, 0.3～0.5 W and 0.2 or more V move into throw out, and the throw out total amount is 3.5 or higher.
18. according to the high-temperature steam turbine rotor of claim 17, wherein when smooth operation, be exposed to top temperature steam high-temperature steam turbine rotor part near running be equivalent to guarantee after 100,000 hours that the throw out total amount is 2.8% or more.
19. high-temperature steam turbine rotor according to claim 17 or 18, wherein this high-temperature steam turbine rotor has original austenite particle diameter average out to 100 μ m or littler tempered bainite single phase structure, even and M, RC type throw out, M, VC, R type throw out, M, QC type throw out and MC type throw out deposit in the bainite single phase structure and are exposed under the top temperature steam when smooth operation and be equivalent to 100,000 hour, the throw out type did not change yet.
20. according to the high-temperature steam turbine rotor of claim 17, wherein Ti and/or N are replaced by Fe and C.
21. high-temperature steam turbine rotor that comprises high temperature steel, described high temperature steel is by weight percentage by 0.25～0.35 C, 0.15 or Si still less, 0.2～0.8 Mn, 0.3～0.6 Ni, 1.6～1.9 Cr, 0.26～0.35 V, 0.6～0.9 Mo, 0.9～1.4 W, 0.001～0.007 N, total amount is that the Fe and the unavoidable impurities of 1.3～1.4 Mo and W/2 and surplus formed, wherein after tempering heat treatment, this high temperature steel is made up of the bainite single phase structure, guarantee by weight percentage 1.0 or more Fe, 0.8～0.9 Cr, 0.4～0.5 Mo, 0.3～0.5 W and 0.2 or more V move into throw out, and the throw out total amount is 3.5 or higher.
22. according to the high-temperature steam turbine rotor of claim 21, wherein when smooth operation, be exposed to top temperature steam high-temperature steam turbine rotor part near running be equivalent to guarantee after 100,000 hours that the throw out total amount is 2.8% or more.
23. high-temperature steam turbine rotor according to claim 21 and 22, wherein this high-temperature steam turbine rotor has original austenite particle diameter average out to 100 μ m or littler tempered bainite single phase structure, even and M, RC type throw out, M, VC, R type throw out, M, QC type throw out and MC type throw out deposit in the bainite single phase structure and are exposed under the top temperature steam when smooth operation and be equivalent to 100,000 hour, the throw out type did not change yet.
24. according to the high-temperature steam turbine rotor of claim 21, wherein Ti and/or N are replaced by Fe and C.
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2004269947A JP4266194B2 (en) | 2004-09-16 | 2004-09-16 | Heat resistant steel, heat treatment method for heat resistant steel, and steam turbine rotor for high temperature |
| JP269947/2004 | 2004-09-16 |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN1749427A true CN1749427A (en) | 2006-03-22 |
| CN100376708C CN100376708C (en) | 2008-03-26 |
Family
ID=35351673
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CNB2005101096888A Expired - Fee Related CN100376708C (en) | 2004-09-16 | 2005-09-16 | Heat-resisting steel, heat treatment method for heat-resisting steel and high-temperature steam turbine rotor |
Country Status (4)
| Country | Link |
|---|---|
| US (1) | US20060054254A1 (en) |
| EP (1) | EP1637615B1 (en) |
| JP (1) | JP4266194B2 (en) |
| CN (1) | CN100376708C (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN107151760A (en) * | 2017-06-12 | 2017-09-12 | 合肥铭佑高温技术有限公司 | A kind of supporting steel pipe of high-temperature service and its production method |
| CN110629126A (en) * | 2019-10-23 | 2019-12-31 | 哈尔滨汽轮机厂有限责任公司 | Material for high-low pressure combined rotor of medium-small turbine at 566 ℃ grade |
Families Citing this family (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US6844131B2 (en) * | 2002-01-09 | 2005-01-18 | Clariant Finance (Bvi) Limited | Positive-working photoimageable bottom antireflective coating |
| US8523519B2 (en) * | 2009-09-24 | 2013-09-03 | General Energy Company | Steam turbine rotor and alloy therefor |
| JP5362764B2 (en) | 2011-04-18 | 2013-12-11 | 株式会社日本製鋼所 | Low alloy metal for geothermal power turbine rotor |
| US9039365B2 (en) * | 2012-01-06 | 2015-05-26 | General Electric Company | Rotor, a steam turbine and a method for producing a rotor |
| CN104109817A (en) * | 2013-04-18 | 2014-10-22 | 曹志春 | High-tungsten-titanium wear-resistant alloy steel |
| JP6213703B1 (en) * | 2016-03-22 | 2017-10-18 | 新日鐵住金株式会社 | ERW steel pipe for line pipe |
| CN105861925A (en) * | 2016-06-13 | 2016-08-17 | 苏州双金实业有限公司 | Steel with high temperature resistance |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6029448A (en) * | 1983-07-29 | 1985-02-14 | Sumitomo Metal Ind Ltd | Steel for high-temperature particle erosion atmosphere |
| US4622067A (en) * | 1985-02-07 | 1986-11-11 | The United States Of America As Represented By The United States Department Of Energy | Low activation ferritic alloys |
| JP3334217B2 (en) | 1992-03-12 | 2002-10-15 | 住友金属工業株式会社 | Low Cr ferritic heat resistant steel with excellent toughness and creep strength |
| JPH06256893A (en) * | 1993-03-04 | 1994-09-13 | Mitsubishi Heavy Ind Ltd | High toughness low alloy steel excellent in high temperature strength |
| DE69527639T2 (en) * | 1994-11-04 | 2003-04-24 | Babcock-Hitachi K.K., Tokio/Tokyo | FERRITIC HEAT-RESISTANT STEEL WITH EXCELLENT STRENGTH AT HIGH TEMPERATURES AND METHOD FOR THE PRODUCTION THEREOF |
| JPH10265909A (en) * | 1997-03-25 | 1998-10-06 | Toshiba Corp | Heat resistant steel with high toughness, turbine rotor, and their production |
| JP3470650B2 (en) * | 1999-08-31 | 2003-11-25 | 住友金属工業株式会社 | High strength low Cr ferritic heat resistant steel with excellent tempering brittleness resistance |
| EP1091010B1 (en) * | 1999-10-04 | 2003-10-22 | Mitsubishi Heavy Industries, Ltd. | Low-alloy heat-resistant steel, process for producing the same, and turbine rotor |
| JP4031603B2 (en) * | 2000-02-08 | 2008-01-09 | 三菱重工業株式会社 | High / low pressure integrated turbine rotor and method of manufacturing the same |
| JP3518515B2 (en) * | 2000-03-30 | 2004-04-12 | 住友金属工業株式会社 | Low / medium Cr heat resistant steel |
| JP3439197B2 (en) | 2001-03-06 | 2003-08-25 | 三菱重工業株式会社 | Low alloy heat resistant steel, heat treatment method thereof, and turbine rotor |
-
2004
- 2004-09-16 JP JP2004269947A patent/JP4266194B2/en active Active
-
2005
- 2005-09-06 US US11/218,659 patent/US20060054254A1/en not_active Abandoned
- 2005-09-13 EP EP05019872.0A patent/EP1637615B1/en not_active Not-in-force
- 2005-09-16 CN CNB2005101096888A patent/CN100376708C/en not_active Expired - Fee Related
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN107151760A (en) * | 2017-06-12 | 2017-09-12 | 合肥铭佑高温技术有限公司 | A kind of supporting steel pipe of high-temperature service and its production method |
| CN110629126A (en) * | 2019-10-23 | 2019-12-31 | 哈尔滨汽轮机厂有限责任公司 | Material for high-low pressure combined rotor of medium-small turbine at 566 ℃ grade |
| CN110629126B (en) * | 2019-10-23 | 2021-07-13 | 哈尔滨汽轮机厂有限责任公司 | Material for high-low pressure combined rotor of medium-small turbine at 566 ℃ grade |
Also Published As
| Publication number | Publication date |
|---|---|
| US20060054254A1 (en) | 2006-03-16 |
| CN100376708C (en) | 2008-03-26 |
| EP1637615A1 (en) | 2006-03-22 |
| EP1637615B1 (en) | 2014-07-16 |
| JP4266194B2 (en) | 2009-05-20 |
| JP2006083432A (en) | 2006-03-30 |
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