cr at 1,100  c was constructed by means of diffusion couples and equilibrated alloys . it was found that nearly 28  at.% of cr can be dissolved in the  phase ( nb7ni6 ) at this temperature , and the solubility of chromium in nbni3 is approximately 5  at.% . under these circumstances the low - temperature ( cubic ) modification of the nbcr2 laves phase can dissolve up to 6  at.% of nickel , but further increase of the ni content ( up to approximately 10  at.% ) stabilizes the hexagonal ( high - temperature ) modification of the laves phase . the presence of this pseudo - ternary compound which is in equilibrium with all binary intermetallics and body - centred cubic ( bcc ) nb- and cr - based solid solutions largely determines the topology of the isotherm at 1,100  c . the formation of this phase was also observed in the reaction zone between nb and ni  cr solid solution when chromium concentration exceeded 15  at.% . cr system is generated mainly by the fact that ni  cr - based alloys are important corrosion - resistant high - temperature materials . their application in combination with the nb - based alloys having a very high specific strength at elevated temperatures might lead to a significant improvement in the high - temperature performance of various structural components . to optimize the fabrication procedure of such composite structures , it is paramount to be able to predict ( and control ) the phases which are formed at the interfaces between niobium and ni  cr alloys upon solid - state bonding and under service conditions . it was repeatedly demonstrated that the optimal starting point for research on any metal  metal interactions is the investigation of the phase equilibria and reactive phase formation in relevant materials systems . cr system has been studied extensively within a limited composition domain bounded by the binary nbni3 and nbcr2 intermetallics and ni- and cr - based solid solutions [ 17 ] . most of the cited work was performed almost 50  years ago . in the investigated composition region the partial liquidus projections , several isothermal sections ( in the temperature range 1,1001,200  c ) and several isopleths have been established . for more details and more complete bibliography , for the higher nb - containing regions of this system only very limited experimental information about phase relations is available . cr system at 1,100  c ( below the liquidus temperature ) and to gain insight into the morphological evolution of the interfacial region between niobium and ni  cr solid solution during the reaction at this temperature . the isothermal cross section through the ternary diagram was constructed by the traditional method of equilibrated alloys and diffusion couple technique . the efficiency of this technique in constructing isothermal cross sections through ternary phase diagrams is higher compared with that when single - phase alloys are used as end - members of the couples because in this case , the chance to  hit  interfaces at which three phases are in equilibrium is much larger . further details concerning the use of diffusion couple techniques in studying phase diagrams can be found in ref . . the microstructure of the reaction zone developed after annealing ( 1,100  c , 196  h ) in the diffusion couple based on pure cr and two - phase alloy with nominal composition ni60nb40 consisting of ( after the equilibration ) -nb7ni6 intermetallic and nbni3 is given in fig .  1 . from the micrograph one can notice that a continuous layer of pseudo - ternary phase ( henceforth designated as  t  ) is a dominant reaction product in this diffusion couple . the product ternary compound appears to be in equilibrium with cr - based solid solution as well as with both constituents of the initial two - phase alloy . the latter indicates a three - phase equilibrium nbni3  +  -nb7ni6  +  t in the nb 1back - scattered electron image ( bei ) showing the morphology of the diffusion zone developed between chromium and two - phase alloy with the nominal composition ni60nb40 after annealing in vacuum at 1,100  c for 196  h. note that the nbni3 domains within the microstructure of the two - phase end - member exhibit a white contrast 
  back - scattered electron image ( bei ) showing the morphology of the diffusion zone developed between chromium and two - phase alloy with the nominal composition ni60nb40 after annealing in vacuum at 1,100  c for 196  h. note that the nbni3 domains within the microstructure of the two - phase end - member exhibit a white contrast 
  when another two - phase material with the nominal composition ni50cr50 , which after equilibration at 1,100  c and quenching in water is a mixture of face - centred cubic ( fcc ) ni - based and body - centred cubic ( bcc ) cr - based solid solutions , was used as the end - member of the diffusion couple , the interfacial reaction with the ni60nb40 alloy also resulted in the formation of a continuous layer of the pseudo - ternary intermetallic ( fig . an interesting feature here is that the product layer of the t phase is not in direct contact with the initial two - phase substrate , but separated from it by the layer of cr - based solid solution . cr system the pseudo - ternary compound t is not in equilibrium with the ni - based solid solution at 1,100  c.fig . 2beis of the reaction zones developed in the annealed ( 1,100  c , 196  h ) diffusion couples based on two - phase alloy with the nominal composition ni50cr50 and a the two - phase alloy ni60nb40 and b pure nb . note that domains of the cr - based solid solution ( cr 
 ss ) present within the microstructure of the ni50cr50 alloy exhibit a dark contrast ( the various phases on the micrographs are denoted by their binary formulae , and t is the pseudo - ternary phase ) beis of the reaction zones developed in the annealed ( 1,100  c , 196  h ) diffusion couples based on two - phase alloy with the nominal composition ni50cr50 and a the two - phase alloy ni60nb40 and b pure nb . note that domains of the cr - based solid solution ( cr 
 ss ) present within the microstructure of the ni50cr50 alloy exhibit a dark contrast ( the various phases on the micrographs are denoted by their binary formulae , and t is the pseudo - ternary phase ) there also exists an equilibrium between cr - based solid solution and nbni3 compound on the nb this can be appreciated from the diffusion zone morphology developed in a ni50cr50/nb couple after reaction at 1,100  c for 196  h ( fig . , it may be suggested that on the nb  ni  cr isotherm at 1,100  c the cr - based solid solution is involved in three - phase equilibria crss  +  nbni3  +  t and crss  +  nbni3  +  niss . moreover , information obtained with the diffusion technique was used as a guide for selecting the compositions of the alloys used to verify the provisionally found equilibria and to determine the boundaries of the phase fields in this ternary system . as it was expected , after equilibrating at 1,100  c for 400  h and quenching ternary alloys with nominal composition ni50cr40nb10 , ni40cr40nb20 , ni55cr5nb40 , and ni15cr35nb50 , they indeed exhibited a three - phase morphology ( fig . the composition of the phases present in the alloys after heat treatment was measured with electron probe microanalysis ( epma ) and the corresponding three - phase equilibria were plotted on the isotherm . it was found that nearly 28  at.% of cr can be dissolved in the  phase ( nb7ni6 ) at this temperature , and the solubility of chromium in the nbni3 is approximately 5  at.%.fig . 3microstructure of the three - phase alloys of the nb  ni  cr system after equilibrating at 1,100  c in vacuum for 196  h and quenching a ni50cr40nb10 , b ni40cr40nb20 , c ni55cr5nb40 , and d ni15cr35nb50 ( the various phases on the micrographs are denoted by their binary formulae . t is the pseudo - ternary phase , and ni 
 ss , cr 
 ss , and nb 
 ss are the ni- , cr- , and nb - based solid solution , respectively ) microstructure of the three - phase alloys of the nb ni  cr system after equilibrating at 1,100  c in vacuum for 196  h and quenching a ni50cr40nb10 , b ni40cr40nb20 , c ni55cr5nb40 , and d ni15cr35nb50 ( the various phases on the micrographs are denoted by their binary formulae . t is the pseudo - ternary phase , and ni 
 ss , cr 
 ss , and nb 
 ss are the ni- , cr- , and nb - based solid solution , respectively ) in order to determine more precisely the phase boundaries on this isotherm a number of equilibrated two- ( and single- ) phase alloys were studied with optical microscopy , epma , and x - ray diffraction ( xrd ) . results of this investigation are summarized in table  1.table  1phases present in equilibrated alloys after annealing at 1,100  c for 400  h and quenchingalloyphases present at 1,100  cni75cr10nb15 
 niss  +  nbni3 
 ni55cr15nb30 
 t  +  nbni3 
 ni30cr5nb65 
 -nb7ni6  +  nbss 
 ni25cr15nb60 
 -nb7ni6  +  nbss ni30cr25nb45 
 -nb7ni6  +  tni30cr45nb25 
 crss  +  tni15cr60nb25 
 crss  +  tni3cr77nb20 
 crss  +  nbcr2 ( lt)ni3cr57nb40 
 nbss  +  nbcr2 ( lt)ni6cr60nb34 
 nbcr2 ( lt)ni8cr58nb34 
 nbcr2 ( lt )  +  tni10cr50nb34 
 t 
 t pseudo - ternary phase , ni 
 ss , cr 
 ss , and nb 
 ss ni- , cr- , and nb - based solid solution , respectively 
 the various phases are denoted by their binary formulae phases present in equilibrated alloys after annealing at 1,100  c for 400  h and quenching 
 t pseudo - ternary phase , ni 
 ss , cr 
 ss , and nb 
 ss ni- , cr- , and nb - based solid solution , respectively 
 the various phases are denoted by their binary formulae with respect to the last three alloys listed in the table some comments concerning the phase determination have to be made . it turned out to be extremely difficult to draw a definite conclusion about the stability region of the pseudo - ternary phase in the nb cr system at 1,100  c on the basis of the results of xrd analysis . three ternary alloys with a fixed nb content of 34  at.% , namely ni6cr60nb34 , ni8cr58nb34 , and ni10cr50nb34 , were annealed at 1,100  c and examined with epma , xrd , and polarized light microscopy . the alloy with the nominal composition ni6cr60nb34 turned out to be a single - phase material and does not show any polarization effect , which is not a surprising finding given the fact that the low - temperature modification of the nbcr2 laves phase of the binary nb  cr system possesses a cubic structure of the mgcu2 type ( c15 , cf24 ) . on the other hand , it was observed that some domains within the microstructure corresponding to the pseudo - ternary phase show a distinct polarization effect , which indicates a crystal symmetry lower than cubic . the third alloy ni10cr50nb34 also appears to be a single - phase material , but contrary to the ni6cr60nb34 alloy , differently oriented grains of the optically anisotropic t phase within the microstructure show distinctly different colours in white polarized light due to reflection pleochroism . as to the nature of the phase t in the nb cr system at this temperature , it is well known that in some instances the crystal structure of a laves phase is dependent on electron concentration   and in the case of the nb cr system it was conjectured that nickel can stabilize the high - temperature ( ht ) modification of nbcr2 . this is consistent with the results of the present work ; at 1,100  c the low - temperature ( lt ) cubic modification of the nbcr2 laves phase can dissolve up to 6  at.% of nickel , whereas further increase of the ni - content ( up to approximately 10  at.% ) stabilizes the ht ( hexagonal mgzn2 type , c14 , hp12 ) modification of the laves phase . finally , the results from phase analysis and concentration measurements in diffusion couples and equilibrated alloys lead to the cross section of the nb 4isothermal cross section through the ternary phase diagram of nb  ni  cr at 1,100  c determined in the present study isothermal cross section through the ternary phase diagram of nb  ni  cr at 1,100  c determined in the present study the microstructure of the reaction zones in the diffusion couples based on niobium and various ni solid - state reaction of ni5  at.% cr solid solution with nb at 1,100  c results in reaction products somewhat similar to those that would be expected ( from the phase diagram ) in a binary nb / ni couple . nbni3 and -nb7ni6 with very low chromium content ( < 0.3  at.% ) , are formed in the transition zone ( fig . it was found that the reaction layer growth follows a parabolic kinetics profile which is indicative of a diffusion - controlled process.fig . 5beis of the reaction zones developed in the diffusion couples based on nb and ni  cr solid solution alloys with different cr content a 5  at.% , b 15  at.% , and c 25  at.% beis of the reaction zones developed in the diffusion couples based on nb and ni  cr solid solution alloys with different cr content a 5  at.% , b 15  at.% , and c 25  at.% however , when 15  at.% of cr was introduced into nickel , interaction in the diffusion couple with nb led to a different morphology . a new feature here is the formation of a continuous ( very thin ) layer of pseudo - ternary compound t between the nbni3 and -nb7ni6 product phases ( fig . it was observed that at this temperature , diffusion zones of the ni  cr / nb couples containing from 15 to 25  at.% of ni exhibit similar reaction pattern , although the relative volume of the pseudo - ternary compound within the reaction product increases with increasing the cr content in the initial end - member ( fig . another characteristic feature of the diffusion zones developed in these samples is a significant enrichment of chromium in the ni - based solution in the vicinity of the alloy  reaction product interface . this implies that in the phase field of the ni - based solid solution on the ternary nb  ni  cr isotherm the diffusion paths proceed in the direction of increasing chromium concentration before entering the single - phase region of nbni3 . this is connected with the higher affinity of ni towards niobium as compared to that for chromium and mass balance requirements . the isothermal cross section through the ternary diagram was constructed by the traditional method of equilibrated alloys and diffusion couple technique . the efficiency of this technique in constructing isothermal cross sections through ternary phase diagrams is higher compared with that when single - phase alloys are used as end - members of the couples because in this case , the chance to  hit  interfaces at which three phases are in equilibrium is much larger . further details concerning the use of diffusion couple techniques in studying phase diagrams can be found in ref . . the microstructure of the reaction zone developed after annealing ( 1,100  c , 196  h ) in the diffusion couple based on pure cr and two - phase alloy with nominal composition ni60nb40 consisting of ( after the equilibration ) -nb7ni6 intermetallic and nbni3 is given in fig .  1 . from the micrograph one can notice that a continuous layer of pseudo - ternary phase ( henceforth designated as  t  ) is a dominant reaction product in this diffusion couple . the product ternary compound appears to be in equilibrium with cr - based solid solution as well as with both constituents of the initial two - phase alloy . the latter indicates a three - phase equilibrium nbni3  +  -nb7ni6  +  t in the nb 1back - scattered electron image ( bei ) showing the morphology of the diffusion zone developed between chromium and two - phase alloy with the nominal composition ni60nb40 after annealing in vacuum at 1,100  c for 196  h. note that the nbni3 domains within the microstructure of the two - phase end - member exhibit a white contrast 
  back - scattered electron image ( bei ) showing the morphology of the diffusion zone developed between chromium and two - phase alloy with the nominal composition ni60nb40 after annealing in vacuum at 1,100  c for 196  h. note that the nbni3 domains within the microstructure of the two - phase end - member exhibit a white contrast 
  when another two - phase material with the nominal composition ni50cr50 , which after equilibration at 1,100  c and quenching in water is a mixture of face - centred cubic ( fcc ) ni - based and body - centred cubic ( bcc ) cr - based solid solutions , was used as the end - member of the diffusion couple , the interfacial reaction with the ni60nb40 alloy also resulted in the formation of a continuous layer of the pseudo - ternary intermetallic ( fig . an interesting feature here is that the product layer of the t phase is not in direct contact with the initial two - phase substrate , but separated from it by the layer of cr - based solid solution . cr system the pseudo - ternary compound t is not in equilibrium with the ni - based solid solution at 1,100  c.fig . 2beis of the reaction zones developed in the annealed ( 1,100  c , 196  h ) diffusion couples based on two - phase alloy with the nominal composition ni50cr50 and a the two - phase alloy ni60nb40 and b pure nb . note that domains of the cr - based solid solution ( cr 
 ss ) present within the microstructure of the ni50cr50 alloy exhibit a dark contrast ( the various phases on the micrographs are denoted by their binary formulae , and t is the pseudo - ternary phase ) beis of the reaction zones developed in the annealed ( 1,100  c , 196  h ) diffusion couples based on two - phase alloy with the nominal composition ni50cr50 and a the two - phase alloy ni60nb40 and b pure nb . note that domains of the cr - based solid solution ( cr 
 ss ) present within the microstructure of the ni50cr50 alloy exhibit a dark contrast ( the various phases on the micrographs are denoted by their binary formulae , and t is the pseudo - ternary phase ) there also exists an equilibrium between cr - based solid solution and nbni3 compound on the nb this can be appreciated from the diffusion zone morphology developed in a ni50cr50/nb couple after reaction at 1,100  c for 196  h ( fig . , it may be suggested that on the nb  ni  cr isotherm at 1,100  c the cr - based solid solution is involved in three - phase equilibria crss  +  nbni3  +  t and crss  +  nbni3  +  niss . moreover , information obtained with the diffusion technique was used as a guide for selecting the compositions of the alloys used to verify the provisionally found equilibria and to determine the boundaries of the phase fields in this ternary system . as it was expected , after equilibrating at 1,100  c for 400  h and quenching ternary alloys with nominal composition ni50cr40nb10 , ni40cr40nb20 , ni55cr5nb40 , and ni15cr35nb50 , they indeed exhibited a three - phase morphology ( fig . the composition of the phases present in the alloys after heat treatment was measured with electron probe microanalysis ( epma ) and the corresponding three - phase equilibria were plotted on the isotherm . it was found that nearly 28  at.% of cr can be dissolved in the  phase ( nb7ni6 ) at this temperature , and the solubility of chromium in the nbni3 is approximately 5  at.%.fig . 3microstructure of the three - phase alloys of the nb  ni  cr system after equilibrating at 1,100  c in vacuum for 196  h and quenching a ni50cr40nb10 , b ni40cr40nb20 , c ni55cr5nb40 , and d ni15cr35nb50 ( the various phases on the micrographs are denoted by their binary formulae . t is the pseudo - ternary phase , and ni 
 ss , cr 
 ss , and nb 
 ss are the ni- , cr- , and nb - based solid solution , respectively ) microstructure of the three - phase alloys of the nb ni  cr system after equilibrating at 1,100  c in vacuum for 196  h and quenching a ni50cr40nb10 , b ni40cr40nb20 , c ni55cr5nb40 , and d ni15cr35nb50 ( the various phases on the micrographs are denoted by their binary formulae . t is the pseudo - ternary phase , and ni 
 ss , cr 
 ss , and nb 
 ss are the ni- , cr- , and nb - based solid solution , respectively ) in order to determine more precisely the phase boundaries on this isotherm a number of equilibrated two- ( and single- ) phase alloys were studied with optical microscopy , epma , and x - ray diffraction ( xrd ) . results of this investigation are summarized in table  1.table  1phases present in equilibrated alloys after annealing at 1,100  c for 400  h and quenchingalloyphases present at 1,100  cni75cr10nb15 
 niss  +  nbni3 
 ni55cr15nb30 
 t  +  nbni3 
 ni30cr5nb65 
 -nb7ni6  +  nbss 
 ni25cr15nb60 
 -nb7ni6  +  nbss ni30cr25nb45 
 -nb7ni6  +  tni30cr45nb25 
 crss  +  tni15cr60nb25 
 crss  +  tni3cr77nb20 
 crss  +  nbcr2 ( lt)ni3cr57nb40 
 nbss  +  nbcr2 ( lt)ni6cr60nb34 
 nbcr2 ( lt)ni8cr58nb34 
 nbcr2 ( lt )  +  tni10cr50nb34 
 t 
 t pseudo - ternary phase , ni 
 ss , cr 
 ss , and nb 
 ss ni- , cr- , and nb - based solid solution , respectively 
 the various phases are denoted by their binary formulae phases present in equilibrated alloys after annealing at 1,100  c for 400  h and quenching 
 t pseudo - ternary phase , ni 
 ss , cr 
 ss , and nb 
 ss ni- , cr- , and nb - based solid solution , respectively 
 the various phases are denoted by their binary formulae with respect to the last three alloys listed in the table some comments concerning the phase determination have to be made . it turned out to be extremely difficult to draw a definite conclusion about the stability region of the pseudo - ternary phase in the nb cr system at 1,100  c on the basis of the results of xrd analysis . three ternary alloys with a fixed nb content of 34  at.% , namely ni6cr60nb34 , ni8cr58nb34 , and ni10cr50nb34 , were annealed at 1,100  c and examined with epma , xrd , and polarized light microscopy . the alloy with the nominal composition ni6cr60nb34 turned out to be a single - phase material and does not show any polarization effect , which is not a surprising finding given the fact that the low - temperature modification of the nbcr2 laves phase of the binary nb  cr system possesses a cubic structure of the mgcu2 type ( c15 , cf24 ) . on the other hand , it was observed that some domains within the microstructure corresponding to the pseudo - ternary phase show a distinct polarization effect , which indicates a crystal symmetry lower than cubic . the third alloy ni10cr50nb34 also appears to be a single - phase material , but contrary to the ni6cr60nb34 alloy , differently oriented grains of the optically anisotropic t phase within the microstructure show distinctly different colours in white polarized light due to reflection pleochroism . as to the nature of the phase t in the nb cr system at this temperature , it is well known that in some instances the crystal structure of a laves phase is dependent on electron concentration   and in the case of the nb cr system it was conjectured that nickel can stabilize the high - temperature ( ht ) modification of nbcr2 . this is consistent with the results of the present work ; at 1,100  c the low - temperature ( lt ) cubic modification of the nbcr2 laves phase can dissolve up to 6  at.% of nickel , whereas further increase of the ni - content ( up to approximately 10  at.% ) stabilizes the ht ( hexagonal mgzn2 type , c14 , hp12 ) modification of the laves phase . finally , the results from phase analysis and concentration measurements in diffusion couples and equilibrated alloys lead to the cross section of the nb 4isothermal cross section through the ternary phase diagram of nb  ni  cr at 1,100  c determined in the present study isothermal cross section through the ternary phase diagram of nb  ni  cr at 1,100  c determined in the present study the microstructure of the reaction zones in the diffusion couples based on niobium and various ni solid - state reaction of ni5  at.% cr solid solution with nb at 1,100  c results in reaction products somewhat similar to those that would be expected ( from the phase diagram ) in a binary nb / ni couple . nbni3 and -nb7ni6 with very low chromium content ( < 0.3  at.% ) , are formed in the transition zone ( fig . it was found that the reaction layer growth follows a parabolic kinetics profile which is indicative of a diffusion - controlled process.fig . 5beis of the reaction zones developed in the diffusion couples based on nb and ni  cr solid solution alloys with different cr content a 5  at.% , b 15  at.% , and c 25  at.% beis of the reaction zones developed in the diffusion couples based on nb and ni  cr solid solution alloys with different cr content a 5  at.% , b 15  at.% , and c 25  at.% however , when 15  at.% of cr was introduced into nickel , interaction in the diffusion couple with nb led to a different morphology . a new feature here is the formation of a continuous ( very thin ) layer of pseudo - ternary compound t between the nbni3 and -nb7ni6 product phases ( fig . it was observed that at this temperature , diffusion zones of the ni  cr / nb couples containing from 15 to 25  at.% of ni exhibit similar reaction pattern , although the relative volume of the pseudo - ternary compound within the reaction product increases with increasing the cr content in the initial end - member ( fig . another characteristic feature of the diffusion zones developed in these samples is a significant enrichment of chromium in the ni - based solution in the vicinity of the alloy this implies that in the phase field of the ni - based solid solution on the ternary nb  ni  cr isotherm the diffusion paths proceed in the direction of increasing chromium concentration before entering the single - phase region of nbni3 . this is connected with the higher affinity of ni towards niobium as compared to that for chromium and mass balance requirements . nickel ( 99.98  % ) , chromium ( 99.95  % ) , and niobium ( 99.98  % ) supplied by goodfellow ( huntingdon , uk ) were used as initial materials . cr alloys ( 550  at.% of cr ) were melted in an arc furnace under argon atmosphere using a non - consumable tungsten electrode . slices of 8    8  mm were cut from the sheets and homogenized under 1  bar of gas mixture ar  +  10  vol% of h2 ( h2o  5  ppm ) at 1,100  c for 100  h. the various ni  cr the ingots of ternary alloys were re - melted five times to improve their homogeneity . the weight loss of the alloys after melting was less than 1  wt% relative . the specimens were annealed in an electro - resistance tube furnace in evacuated quartz ampoules at 1,100  c . the diffusion couples were prepared and heat - treated in a vacuum furnace ( ca . 5    10  mbar ) under an external load of approximately 2  mpa . temperature control was carried out within 2  c accuracy . for a typical experiment , the cooling rate of the sample in the vacuum furnace was about 600  c / h . after annealing and standard metallographic preparation the diffusion couples and equilibrated alloys were examined by optical microscopy , scanning electron microscopy ( sem ) , and epma . owing to the coarse structure of the annealed alloys , xrd analysis was performed with a cylindrical texture camera using nickel - filtered kcu radiation . this article is distributed under the terms of the creative commons attribution license which permits any use , distribution , and reproduction in any medium , provided the original author(s ) and the source are credited .
abstractthe isothermal cross section through the ternary phase diagram nb  ni 
 cr at 1,100  c was constructed by means of diffusion couples and equilibrated alloys . 
 it was found that nearly 28  at.% of cr can be dissolved in the  phase ( nb7ni6 ) at this temperature , and the solubility of chromium in nbni3 is approximately 5  at.% . under these circumstances 
 the low - temperature ( cubic ) modification of the nbcr2 laves phase can dissolve up to 6  at.% of nickel , but further increase of the ni content ( up to approximately 10  at.% ) stabilizes the hexagonal ( high - temperature ) modification of the laves phase . 
 the presence of this pseudo - ternary compound which is in equilibrium with all binary intermetallics and body - centred cubic ( bcc ) nb- and cr - based solid solutions largely determines the topology of the isotherm at 1,100  c . 
 the formation of this phase was also observed in the reaction zone between nb and ni  cr solid solution when chromium concentration exceeded 15  at.%.graphical abstract