The Udimet 500 nickel base superalloy blade exposed for 50000 hours in land base gas turbine working conditions faced the structure degradation. Six different heat treatments procedures have been applied (the blades were exposed at 900 °C and 1000 °C for different periods with maximum hold of 2500 hours) to rejuvenate the degraded structure. Metallographic work was performed, generally, aging at both temperatures modify the gamma prime size, morphology and distribution characteristics substantially. The volume fraction of secondary gamma prime decreased with increasing aging time

I. Mamuzić

J. Zrnik

P. Wangyao

S. Klaijumrang

S. Polsilapa

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METALURGIJA 46 (2007) 3, 195-199 195P. WANGYAO et al.: RESTORATION AND THERMAL STABILITY INVESTIGATION OF INTERMETALLIC ...Received - Primljeno: 2006-06-18ISSN 0543-5846METABK 46 (3) 195-199 (2007)UDC - UDK 669.248:620.18:621.78.621.438=111S. KLAIJUMRANGP. Wangyao, Metallurgy and Materials Science Research Institute Uni-versity of Chulalongkorn, Bangkok, Thailand, J. Zrnik, Comtes FHT, Plzen, Czech Republic, Faculty of Metallurgy Technical University of -sity of Zagreb, Sisak, Croatia, S. Polsilapa, S. Klaijumrang, Faculty of Engineering University of Kasetsart, Bangkok, ThailandRESTORATION AND THERMAL STABILITY INVESTIGATION OF INTERMETLLICPHASE IN EXPOSED NICKEL BASE SUPERALLOY UDIMET 500 TURBINE BLADESINTRODUCTIONNickel base superalloys are structural materials, which are employed at high temperature and resisting variable ther-momechanical loading. The microstructure and mechanical properties can be related to their chemical composition and heat treatment process. The most frequently used heat treat-ment, at which solution treatment is followed by a single or a double aging sequence, secures gamma prime precipitation within the grains interior, and as well discrete carbides M23C6grain boundary carbides, to increase creep resistance [1]. The proper chemical composition of alloy and heat treated microstructure can provide stability of present phases, and consequently adequate high strength and good ductility even after long-term thermal exposure.The mechanical behavior of nickel base superalloys is very strongly related to the alloy microstructures. The The Udimet 500 nickel base superalloy blade exposed for 50000 hours in land base gas turbine working condi-tions faced the structure degradation. Six different heat treatments procedures have been applied (the blades were exposed at 900 °C and 1000 °C for different periods with maximum hold of 2500 hours) to rejuvenate the degraded structure. Metallographic work was performed, generally, aging at both temperatures modify the gamma prime size, morphology and distribution characteristics substantially. The volume fraction of secondary gamma prime decreased with increasing aging time.Key words: nickel base superalloy, microstructure, heat treatment (HT), blade structure degradation- Lopatice plinskih turbina nikljove super legure Udimet 500 tijekom uporabe sekundarnog gama zrna smanjuje se porastom vremena starenja.nikljova super legura, mikrostruktura, toplinska obradba (TO), degradacija strukture lopaticesuperalloy microstructures continually change with time at the elevated temperatures. In heat treated alloys, the gamma prime particles are arranged in a structure, which results in an optimum balance of tensile, fatigue, and creep properties [2]. A number of previous research works had been carried out to investigate these microstructure-me-chanical properties relationships [3 - 5].The use of these materials is very expensive and re-quires for the safety and economic reason a repair process providing the re-establishment of the initial properties in exposed parts after long term of using [6]. The heat-treat-ment processes for nickel-base superalloys continue in upgrading optimizing the mechanical and physical prop-erties [7 - 9]. This makes the selection of heat treatment parameters increasingly challenging.Udimet 500 is a gamma prime precipitation-strength-ened nickel base superalloy which is widely used as turbine blades in hot sections of gas turbine engines due to its outstanding strength properties at high temperature as well as excellent hot corrosion resistance. Udimet 500 contains substantial amount of Al and Ti together about 6 wt. %, which provides precipitation strengthening of ordered L12 intermetallic Ni3 (Al, Ti) gamma prime phase. METALURGIJA 46 (2007) 3, 195-199196P. WANGYAO et al.: RESTORATION AND THERMAL STABILITY INVESTIGATION OF INTERMETALLIC ...The size, distribution and the morphology of gamma prime single and double aging treatment procedures are utilized at heat treatment of this alloy.The aim of this study is to determine the most suitable and practicable repair condition in exposed turbine blades. of long-term exposed gas turbine blades were performed. Then the stability of structure received after blade rejuve-nation was evaluated at two annealing temperatures with exposure time varying.MATERIAL AND EXPERIMENTAL PROCEDUREThe experimental material for structural analysis were as-cast blades from nickel base superalloy Udimet 500 exposed 50000 hour in service, operated by Electricity Generating of Thailand (EGAT). The he chemical com-position of the nickel base superalloy was as follows (in wt. %): 18% Cr, 17% Co, 3% Ti, 3% Al, 4% Mo, 0,1% C,2% Fe, and balance nickel (53 %).The plates of about 1 cm2 were cut from the most severe degradation zone of leading edge of the turbine blades. The specimens were heat treated according to heat treatment conditions including solution treatment and two step ag-ing in vacuum furnace. The rejuvenation heat treatments performed are stated in Table 1.The treated specimens were then aged at temperatures of 900 °C and 1000 °C for 500, 1000, 1500, 2000, and/or 2500 hours in order to evaluate the coarsening behavior of gamma prime particles. All sectioned samples after ther-mal treatments were prepared by standard metallographic techniques and subsequently etched in Marble etchant. The microstructure characteristics of thermally exposed samples were observed by scanning electron microscope using secondary electron mode and image analyzer to size and volume fraction of the gamma prime precipitates were determined.EXPERIMENTAL RESULTS AND DISCUSSIONThe microstructure of exposed bladeThe microstructure of cast Udimet 500 superalloy generally consists of extensive precipitation of ordered L12 ’ intermetallic phase within dendrite core and in the interdendritic region. Carbides predominantly M23C6 typedeposited along grain boundaries and MC type in vicinity are usually present in as-cast structure. Microsegregation equilibrium gamma  - gamma prime ’ eutectic.Scanning electron microscopy micrograph of the de-graded blade structure, obtained from transverse sections of the exposed blade, is shown in Figure 1. Due to long term operation service of the blades the changes the bimodal gam-ma prime precipi-tates are apparent. The morphology, size, distribution characteristics and volume frac-tion, of the both precipitates, the primary and  sec-ondary gamma primes, are de-graded. The mor-phology of coarse -tates exhibits also morphological instability. The formerly cuboidal precipi-tates became irregular in shape and small gamma prime distribution is not uniform. The changes of the grain bound-ary carbides were observed as well. The local coarsening of Cr23C6 carbides deposited along grain boundaries and their dissolve or agglomerate, resulting in variation of amount ads morphology. Frequently in vicinity of coarse carbides and/or carbide residues the pores were found. The reason for their appearance is either creep process or local incipi-ent melting. The degree of degradation, as measured by the gamma prime particle size, is directionally proportional to time and temperature of exposure.-tion in service comparing to the microstructure of the root section. In virgin as-cast structure of the blade the primary gamma prime particle size was about 0,4 m and second-ary gamma prime precipitate size was about 0,1 m. The primary gamma prime particles have grown larger chang-ing round shape morphology and the secondary gamma observed. It is expected that these structure changes modify METALURGIJA 46 (2007) 3, 195-199 197P. WANGYAO et al.: RESTORATION AND THERMAL STABILITY INVESTIGATION OF INTERMETALLIC ...the high temperature creep resistance of the blade materials. Applying a refurbishment treatment appears as less expen-sive alternative to extend the blade life time.  In order to recover microstructure in exposed blade the effective heat treatment process should be found to obtain the structure of similar characteristics like in the virgin blade.The microstructure of heat treated alloyAccording to the previous works, repeating the standard heat treatment sequence with aim to recover degraded mi-crostructure of nickel base superalloy Incomel 738 exposed and properties were not fully recovered. In this experimen-tal, for the Udimet 500 exposed blade, the six different heat treatment schedules which were used are stated in Table 1. The formation of new microstructure in exposed To restrict the number of parameters, which can modify the gamma prime characteristics in time of treatment, the only temperature of second aging was gradually increasing and hold time was extended in individual schedules. The microstructure of blade obtained after the standard heat treatment is presented in Figure 2. Resulting gamma prime precipitates are of duplex size. Comparing this restored structure with that one observed in exposed blade the progress in struc-ture restoration is evident. Under these heat treat-ment condition, the alloy exhibits bimodal morphol-ogy of gamma prime precipi-tates. The coarse gamma primes, which precipitated during the primary aging process at higher temperature, possess the round shape and they are accidentally distributed in gamma matrix. The quite and volume fraction of these coarser gamma primes. The secondary gamma primes, which precipitated at lower distributed in gamma matrix.With increasing aging temperature and holding time, the morphological characteristics and distribution of bimodal gamma prime precipitates have not changed evi-dently. The gamma morphology is very quite similar to that of the standard heat treatment. Performing all treatments, -tated in matrix at different aging temperatures, exhibit the round shape, re-gardless the tem-perature of the secondary aging was increasing when compari-son with the stan-dard heat treat-ment schedule for Udimet 500, (see Table 1.).  The representat ive microstructures for two different temperatures of the secondary aging and the same holding time are pre-sented in Figure 3. and Figure 4. The precipitation charac-teristics, received at individual heat treatment con-ditions, do not display expres-sive differences in gamma prime morphology and distribution with increasing aging temperature and extending hold time. Analyzing the results ob-tained at this reju-and hold time at the secondary aging stage did not show the substantial difference considering the gamma prime morphology and distribution.Effect of thermal exposureon gamma prime precipitates characteristicsTwo different temperatures of 900 °C and 1000 °C and various hold times were selected for investigation of thermal stability of gamma primes in rejuvenated blades. It was observed that annealing at 900 °C already resulted in fast coarsening of duplex size gamma prime received in initially heat treated blade samples. Extending the holding time and increasing temperature the gamma prime size increases. Considering the mechanism of gamma prime coarsening, (less stable) and by enriching the gamma matrix with ele-ments, which contributes to precipitate growth (Al, Ti), the more stable gamma primes grow larger. We do not expect that at this annealing temperature the gamma prime would initially precipitate in gamma matrix and then to grow. METALURGIJA 46 (2007) 3, 195-199198P. WANGYAO et al.: RESTORATION AND THERMAL STABILITY INVESTIGATION OF INTERMETALLIC ...The dissolution process of gamma prime precipitates at temperature of 900 °C is clearly seen for in Figure 5. The coarsening process of gamma prime is more ef-fective as hold time increases, and consequently the heterogeneity in gamma prime size is then more distinctive for all schedules of heat treatments, Fig-ure 6.Heating at in-creased tempera-ture of 1000 °Cresulted in more drastic coarsening of gamma prime particles for all hold times. The process of gamma prime coarsen-ing was observed already after of 500 h of thermal exposure. The gamma prime coarsened into round shape at the beginning of the process, Figure7. When blade was exposed to longer holds of 2000 h the gamma prime possesses the mixed mor-phology of qua-sicuboidal shape, like is displayed in Figure 8. From the results of metal-ography analysis can be concluded that there was not observed a sub-thermal stability of duplex gamma prime precipitate re-garding the heat treatment schedule applied. The statistical results concerning the change of gamma prime size in de-pendence of the applied thermal treatment and conducting long term annealing are shown in Figure 9. These results have been ob-tained from mea-surements of the gamma prime size which was modi-of the heat treat-ment schedules (Table 1.) and by different holding times at anneal-ing temperature of 900 °C and 1000 °C. From the dependences is clearly seen that there is continuous gamma prime size increase as holding time increases for both annealing tem-perature. Consequently the results suggest that for Udimet 500 superalloy, exposed in land base gas turbine, already at lower exposure temperature of 900 °C the gamma prime -sure gas turbine can be relevant. Analyzing the results on the effect of annealing process, there was not observed the substantial difference, considering the prior two step aging, on gamma prime coarsening behavior in individual METALURGIJA 46 (2007) 3, 195-199 199P. WANGYAO et al.: RESTORATION AND THERMAL STABILITY INVESTIGATION OF INTERMETALLIC ...AcknowledgementOne of the authors (J. Zrnik) gratefully acknowledge Slovak Republic for present research in frame of COST 538 Action.structures. Concerning the evaluation of alloy thermal stability for applied conditions it could be concluded that all obtained microstructures after annealing was not to for long term exposure at high temperatures. In all annealed specimens the results showed the continuous gamma prime coarsening was more detrimental with increasing exposure time for both temperatures. It is only natural that higher temperature accelerated the gamma primes morphology changes in larger extent.CONCLUSIONSThe experimental was carried out with an aim to evaluate the structural degradation of the turbine blades cast from Rudiment 500 nickel base super alloy, prior long term exposed in land base gas turbine. The extent of microstructure degradation was evaluated. The series of rejuvenation heat treatments were conducted with aim to recover gamma prime characteristics. The evolution of gamma prime morphology, size and distribution at solu-tion and two steps aging treatment has been investigated. With increasing temperature and hold time at the second aging the morphological changes of primary gamma prime appeared at the highest temperature applied. The thermal stability of restored gamma prime precipitates in blades, which exhibits duplex size after rejuvenation treatment, has been then tested at two different annealing tempera-tures for the different holding time. The gamma prime morphology changes and reduction of volume fraction was observed at both annealing temperatures. The higher annealing temperature of 1000 °C promoted formation of gamma prime instability.REFERENCES[1] R. M. F. Jones, L. A. Jackman: The structural evolution of superalloy ingot during hot working, JOM 49 (1999) 4, 27 - 31.[2] T. E. Howson, W. H. Couts: Thermomechanical Processing of Superal-loys in Superalloys, Supercomposites and Superceramics, edited by [3] C. H. Symonds: Hot working Chapter in The Nimonic Alloys & Other-Base High Temperature Alloys, edited by Betteridge, W. & Heslop, J., Edward Arnold (1974), 129 - 149.[4] L. A. Jackman: Forming, Fabrication and Heat Treatment of Superal-loys, in Superalloys Source Book, ASM (1984), 217 - 233.[5] T. H. Courtney: Mechanical Behavior of Materials, McGraw-Hill(Publishers) Ltd., London (1990).[6] A. K. Koul, J. P. Immarigeon, R. D. Dainty, P. C. Patnaik, Proceed-ings of ASM 1993 Materials Congress, Materials Week ’93, October 17-21 (1993), Pittsburgh, USA, 69.[7] P. Wangyao, T. Korath, T. Harnvirojkul, W. Homkajai, Journal of Metals, Materials and Minerals 14 (2004) 1, 49 - 59.[8] J. A. Daleo, H. A. Ellison, D.H. Boone, Journal of Engineering for Gas Turbines and Power 124 (2002), 571 - 579.[9] J. Zrník, P. Strunz, V. Vrchovinský, O. Muransky, Z. Novy, A. Wie-denmann, Journal of Material Science & Engineering A 387-389 (2004), 728 - 733.[10] P. Wangyao, J. Zrnik, S. Polsilapa, E. Nisaratanaporn, W. Homkrajai, Proceedings of  the 8th Liege Conference “Materials for Advanced Power Engineering 2006”, 53 (2006), 377 (Part I).

English

Restoration and Thermal Stability Investigation of Intermetllic Phase in Exposed Nickel Base Superalloy Udimet 500 Turbine Blades

Wangyao, P.

Zrnik, J.

Mamuzić, I.

Polsilapa, S.

Klaijumrang, S.

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Hrčak - Portal of scientific journals of Croatia

METALURGIJA 46 (2007) 3, 195-199 195P. WANGYAO et al.: RESTORATION AND THERMAL STABILITY INVESTIGATION OF INTERMETALLIC ...Received - Primljeno: 2006-06-18????????????????????????????????????????????????????????????????????????ISSN 0543-5846METABK 46 (3) 195-199 (2007)UDC - UDK 669.248:620.18:621.78.621.438=111??? ????????????????????? ?????????????????????S. KLAIJUMRANGP. Wangyao, Metallurgy and Materials Science Research Institute Uni-versity of Chulalongkorn, Bangkok, Thailand, J. Zrnik, Comtes FHT, Plzen, Czech Republic, Faculty of Metallurgy Technical University of ??????????????????????????????????????????????????????????????????-sity of Zagreb, Sisak, Croatia, S. Polsilapa, S. Klaijumrang, Faculty of Engineering University of Kasetsart, Bangkok, ThailandRESTORATION AND THERMAL STABILITY INVESTIGATION OF INTERMETLLICPHASE IN EXPOSED NICKEL BASE SUPERALLOY UDIMET 500 TURBINE BLADESINTRODUCTIONNickel base superalloys are structural materials, which are employed at high temperature and resisting variable ther-momechanical loading. The microstructure and mechanical properties can be related to their chemical composition and heat treatment process. The most frequently used heat treat-ment, at which solution treatment is followed by a single or a double aging sequence, secures gamma prime precipitation within the grains interior, and as well discrete carbides M23C6grain boundary carbides, to increase creep resistance [1]. The proper chemical composition of alloy and heat treated microstructure can provide stability of present phases, and consequently adequate high strength and good ductility even after long-term thermal exposure.The mechanical behavior of nickel base superalloys is very strongly related to the alloy microstructures. The The Udimet 500 nickel base superalloy blade exposed for 50000 hours in land base gas turbine working condi-tions faced the structure degradation. Six different heat treatments procedures have been applied (the blades were exposed at 900 °C and 1000 °C for different periods with maximum hold of 2500 hours) to rejuvenate the degraded structure. Metallographic work was performed, generally, aging at both temperatures modify the gamma prime size, morphology and distribution characteristics substantially. The volume fraction of secondary gamma prime decreased with increasing aging time.Key words: nickel base superalloy, microstructure, heat treatment (HT), blade structure degradation????????????????????????????????????????????????????????????????????????????????????? ?? ???????????????-????????????????????????????????? Lopatice plinskih turbina nikljove super legure Udimet 500 tijekom uporabe ????????????????????????????? ?????????????????????????????????????????????????????????????????????????????????????????????????????????????????????????????????????????????????????????????????? ???????? ???????? ?????????????????????????????????????????????????????? ???????????????????????????????????????????????????????????????????????????????? ???????????? ???????????????? ???????????????????????????????????????????????????? ????????????????sekundarnog gama zrna smanjuje se porastom vremena starenja.??????????????? nikljova super legura, mikrostruktura, toplinska obradba (TO), degradacija strukture lopaticesuperalloy microstructures continually change with time at the elevated temperatures. In heat treated alloys, the gamma prime particles are arranged in a structure, which results in an optimum balance of tensile, fatigue, and creep properties [2]. A number of previous research works had been carried out to investigate these microstructure-me-chanical properties relationships [3 - 5].The use of these materials is very expensive and re-quires for the safety and economic reason a repair process providing the re-establishment of the initial properties in exposed parts after long term of using [6]. The heat-treat-ment processes for nickel-base superalloys continue in upgrading optimizing the mechanical and physical prop-erties [7 - 9]. This makes the selection of heat treatment parameters increasingly challenging.Udimet 500 is a gamma prime precipitation-strength-ened nickel base superalloy which is widely used as turbine blades in hot sections of gas turbine engines due to its outstanding strength properties at high temperature as well as excellent hot corrosion resistance. Udimet 500 contains substantial amount of Al and Ti together about 6 wt. %, which provides precipitation strengthening of ordered L12 intermetallic Ni3 (Al, Ti) gamma prime phase. METALURGIJA 46 (2007) 3, 195-199196P. WANGYAO et al.: RESTORATION AND THERMAL STABILITY INVESTIGATION OF INTERMETALLIC ...The size, distribution and the morphology of gamma prime ???????????????????????????????????????????????????????single and double aging treatment procedures are utilized at heat treatment of this alloy.The aim of this study is to determine the most suitable and practicable repair condition in exposed turbine blades. ??????????????????????????????????????????????????????????of long-term exposed gas turbine blades were performed. Then the stability of structure received after blade rejuve-nation was evaluated at two annealing temperatures with exposure time varying.MATERIAL AND EXPERIMENTAL PROCEDUREThe experimental material for structural analysis were as-cast blades from nickel base superalloy Udimet 500 exposed 50000 hour in service, operated by Electricity Generating of Thailand (EGAT). The he chemical com-position of the nickel base superalloy was as follows (in wt. %): 18% Cr, 17% Co, 3% Ti, 3% Al, 4% Mo, 0,1% C,2% Fe, and balance nickel (53 %).The plates of about 1 cm2 were cut from the most severe degradation zone of leading edge of the turbine blades. The specimens were heat treated according to heat treatment conditions including solution treatment and two step ag-ing in vacuum furnace. The rejuvenation heat treatments performed are stated in Table 1.The treated specimens were then aged at temperatures of 900 °C and 1000 °C for 500, 1000, 1500, 2000, and/or 2500 hours in order to evaluate the coarsening behavior of gamma prime particles. All sectioned samples after ther-mal treatments were prepared by standard metallographic techniques and subsequently etched in Marble etchant. The microstructure characteristics of thermally exposed samples were observed by scanning electron microscope using secondary electron mode and image analyzer to ???????????????????????????????????????????????????????size and volume fraction of the gamma prime precipitates were determined.EXPERIMENTAL RESULTS AND DISCUSSIONThe microstructure of exposed bladeThe microstructure of cast Udimet 500 superalloy generally consists of extensive precipitation of ordered L12 ?’ intermetallic phase within dendrite core and in the interdendritic region. Carbides predominantly M23C6 typedeposited along grain boundaries and MC type in vicinity ????????????????????? ??????????????????????????????????????are usually present in as-cast structure. Microsegregation ????????????????????????????????????????????????????????equilibrium gamma ? - gamma prime ?’ eutectic.Scanning electron microscopy micrograph of the de-graded blade structure, obtained from transverse sections of the exposed blade, is shown in Figure 1. Due to long term operation service of the blades the changes the bimodal gam-ma prime precipi-tates are apparent. The morphology, size, distribution characteristics and volume frac-tion, of the both precipitates, the primary and  sec-ondary gamma primes, are de-graded. The mor-phology of coarse ????????????????-tates exhibits also morphological instability. The formerly cuboidal precipi-tates became irregular in shape and small gamma prime distribution is not uniform. The changes of the grain bound-ary carbides were observed as well. The local coarsening of Cr23C6 carbides deposited along grain boundaries and their ??????????????????????????????????????????????????????dissolve or agglomerate, resulting in variation of amount ads morphology. Frequently in vicinity of coarse carbides and/or carbide residues the pores were found. The reason for their appearance is either creep process or local incipi-ent melting. The degree of degradation, as measured by the gamma prime particle size, is directionally proportional to time and temperature of exposure.????????????????????????? ?????? ??????????????????-tion in service comparing to the microstructure of the root section. In virgin as-cast structure of the blade the primary gamma prime particle size was about 0,4 ?m and second-ary gamma prime precipitate size was about 0,1 ?m. The primary gamma prime particles have grown larger chang-ing round shape morphology and the secondary gamma ???????????????????? ????????????????????????????????? ???observed. It is expected that these structure changes modify METALURGIJA 46 (2007) 3, 195-199 197P. WANGYAO et al.: RESTORATION AND THERMAL STABILITY INVESTIGATION OF INTERMETALLIC ...the high temperature creep resistance of the blade materials. Applying a refurbishment treatment appears as less expen-sive alternative to extend the blade life time.  In order to recover microstructure in exposed blade the effective heat treatment process should be found to obtain the structure of similar characteristics like in the virgin blade.The microstructure of heat treated alloyAccording to the previous works, repeating the standard heat treatment sequence with aim to recover degraded mi-crostructure of nickel base superalloy Incomel 738 exposed ?????????????????????? ????????????????????? ?????????????and properties were not fully recovered. In this experimen-tal, for the Udimet 500 exposed blade, the six different heat treatment schedules which were used are stated in Table 1. The formation of new microstructure in exposed ?????? ??? ?????????????????????????????????????????????To restrict the number of parameters, which can modify the gamma prime characteristics in time of treatment, the only temperature of second aging was gradually increasing and hold time was extended in individual schedules. The microstructure of blade obtained after the standard heat treatment is presented in Figure 2. Resulting gamma prime precipitates are of duplex size. Comparing this restored structure with that one observed in exposed blade the progress in struc-ture restoration is evident. Under these heat treat-ment condition, the alloy exhibits bimodal morphol-ogy of gamma prime precipi-tates. The coarse gamma primes, which precipitated during the primary aging process at higher temperature, possess the round shape and they are accidentally distributed in gamma matrix. The quite ?????????????????????????????????? ?????????????????????and volume fraction of these coarser gamma primes. The secondary gamma primes, which precipitated at lower ???????????????????????????????????????????????????????distributed in gamma matrix.With increasing aging temperature and holding time, the morphological characteristics and distribution of bimodal gamma prime precipitates have not changed evi-dently. The gamma morphology is very quite similar to that of the standard heat treatment. Performing all treatments, ??????????????????????? ??????????????????? ????????????-tated in matrix at different aging temperatures, exhibit the round shape, re-gardless the tem-perature of the secondary aging was increasing when compari-son with the stan-dard heat treat-ment schedule for Udimet 500, (see Table 1.).  The representat ive microstructures for two different temperatures of the secondary aging and the same holding time are pre-sented in Figure 3. and Figure 4. The precipitation charac-teristics, received at individual heat treatment con-ditions, do not display expres-sive differences in gamma prime morphology and distribution with increasing aging temperature and extending hold time. Analyzing the results ob-tained at this reju-????????????????????????? ??????????????????????????????and hold time at the secondary aging stage did not show the substantial difference considering the gamma prime morphology and distribution.Effect of thermal exposureon gamma prime precipitates characteristicsTwo different temperatures of 900 °C and 1000 °C and various hold times were selected for investigation of thermal stability of gamma primes in rejuvenated blades. It was observed that annealing at 900 °C already resulted in fast coarsening of duplex size gamma prime received in initially heat treated blade samples. Extending the holding time and increasing temperature the gamma prime size increases. Considering the mechanism of gamma prime coarsening, ??? ????????????????????????????????????????????????? ??????(less stable) and by enriching the gamma matrix with ele-ments, which contributes to precipitate growth (Al, Ti), the more stable gamma primes grow larger. We do not expect that at this annealing temperature the gamma prime would initially precipitate in gamma matrix and then to grow. METALURGIJA 46 (2007) 3, 195-199198P. WANGYAO et al.: RESTORATION AND THERMAL STABILITY INVESTIGATION OF INTERMETALLIC ...The dissolution process of gamma prime precipitates at temperature of 900 °C is clearly seen for in Figure 5. The coarsening process of gamma prime is more ef-fective as hold time increases, and consequently the heterogeneity in gamma prime size is then more distinctive for all schedules of heat treatments, Fig-ure 6.Heating at in-creased tempera-ture of 1000 °Cresulted in more drastic coarsening of gamma prime particles for all hold times. The process of gamma prime coarsen-ing was observed already after of 500 h of thermal exposure. The gamma prime coarsened into round shape at the beginning of the process, Figure7. When blade was exposed to longer holds of 2000 h the gamma prime possesses the mixed mor-phology of qua-sicuboidal shape, like is displayed in Figure 8. From the results of metal-ography analysis can be concluded that there was not observed a sub-???????????????????????????????????????????????????????????thermal stability of duplex gamma prime precipitate re-garding the heat treatment schedule applied. The statistical results concerning the change of gamma prime size in de-pendence of the applied thermal treatment and conducting long term annealing are shown in Figure 9. These results have been ob-tained from mea-surements of the gamma prime size which was modi-??????? ??????????of the heat treat-ment schedules (Table 1.) and by different holding times at anneal-ing temperature of 900 °C and 1000 °C. From the dependences is clearly seen that there is continuous gamma prime size increase as holding time increases for both annealing tem-perature. Consequently the results suggest that for Udimet 500 superalloy, exposed in land base gas turbine, already at lower exposure temperature of 900 °C the gamma prime ????????????????????????????????????????????????????????????-sure gas turbine can be relevant. Analyzing the results on the effect of annealing process, there was not observed the substantial difference, considering the prior two step aging, on gamma prime coarsening behavior in individual METALURGIJA 46 (2007) 3, 195-199 199P. WANGYAO et al.: RESTORATION AND THERMAL STABILITY INVESTIGATION OF INTERMETALLIC ...AcknowledgementOne of the authors (J. Zrnik) gratefully acknowledge ?????????????????????????????????????????????????????????Slovak Republic for present research in frame of COST 538 Action.structures. Concerning the evaluation of alloy thermal stability for applied conditions it could be concluded that all obtained microstructures after annealing was not to ????????????????????????????????????????????????????????for long term exposure at high temperatures. In all annealed specimens the results showed the continuous gamma prime coarsening was more detrimental with increasing exposure time for both temperatures. It is only natural that higher temperature accelerated the gamma primes morphology changes in larger extent.CONCLUSIONSThe experimental was carried out with an aim to evaluate the structural degradation of the turbine blades cast from Rudiment 500 nickel base super alloy, prior long term exposed in land base gas turbine. The extent of microstructure degradation was evaluated. The series of rejuvenation heat treatments were conducted with aim to recover gamma prime characteristics. The evolution of gamma prime morphology, size and distribution at solu-tion and two steps aging treatment has been investigated. With increasing temperature and hold time at the second aging the morphological changes of primary gamma prime appeared at the highest temperature applied. The thermal stability of restored gamma prime precipitates in blades, which exhibits duplex size after rejuvenation treatment, has been then tested at two different annealing tempera-tures for the different holding time. The gamma prime morphology changes and reduction of volume fraction was observed at both annealing temperatures. The higher annealing temperature of 1000 °C promoted formation of gamma prime instability.REFERENCES[1] R. M. F. Jones, L. A. Jackman: The structural evolution of superalloy ingot during hot working, JOM 49 (1999) 4, 27 - 31.[2] T. E. Howson, W. H. Couts: Thermomechanical Processing of Superal-loys in Superalloys, Supercomposites and Superceramics, edited by ????????? ?? ??????????????? ??????????????????????????????????????[3] C. H. Symonds: Hot working Chapter in The Nimonic Alloys & Other-Base High Temperature Alloys, edited by Betteridge, W. & Heslop, J., Edward Arnold (1974), 129 - 149.[4] L. A. Jackman: Forming, Fabrication and Heat Treatment of Superal-loys, in Superalloys Source Book, ASM (1984), 217 - 233.[5] T. H. Courtney: Mechanical Behavior of Materials, McGraw-Hill(Publishers) Ltd., London (1990).[6] A. K. Koul, J. P. Immarigeon, R. D. Dainty, P. C. Patnaik, Proceed-ings of ASM 1993 Materials Congress, Materials Week ’93, October 17-21 (1993), Pittsburgh, USA, 69.[7] P. Wangyao, T. Korath, T. Harnvirojkul, W. Homkajai, Journal of Metals, Materials and Minerals 14 (2004) 1, 49 - 59.[8] J. A. Daleo, H. A. Ellison, D.H. Boone, Journal of Engineering for Gas Turbines and Power 124 (2002), 571 - 579.[9] J. Zrník, P. 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Restoration and Thermal Stability Investigation of Intermetllic Phase in Exposed Nickel Base Superalloy Udimet 500 Turbine Blades

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