Detection of Ni–Sn phases in temper embrittled Ni–Cr steels
A GENERIC problem in ferritic steels is the reduction in the grain boundary cohesive strength produced by the segregation of trace impurities of Groups IVB and VB of the Periodic Table. Such segregation results in a deterioration in mechanical properties produced, for example, by reversible temper embittlement1 and it also promotes enhanced susceptibility to a range of environmental enhanced cracking processes2–4. It has long been recognised that the embrittlement of steels is enhanced by the presence of certain alloy elements, that is Ni, Cr or Mn, and measurements using Auger electron spectroscopy (AES)5–7 have demonstrated that specific combinations of alloy and impurity elements cosegregate to the boundaries, for example, Ni+Sn, Ni+Sb, Cr+P. These observations can be rationalised using Guttmann's phenomenological theory8 which attributes the increased driving force for segregation to a positive interaction between alloy and impurity solute atoms. Previous investigations1,9–11 have failed to detect the presence of any three dimensional phase using conventional transmission electron microscopy and it is generally considered that the alloy element–trace impurity atoms form two dimensional phases at the boundaries. The only direct evidence for such alloy–impurity interactions and phase formation has been obtained using Mössbauer spectroscopy12,13 but it is not possible using this technique to draw any positive conclusions regarding the location of such compounds. Measurements on a pure Fe-3.5 wt% Ni alloy doped with 119Sn12 showed that Ni atoms associate preferentially with Sn atoms during tempering at 650°C and the marked change in the spectrum observed on ageing at 500°C, within the embrittling temperature range, is consistent with the formation of a Ni–Sn compound (Ni3Sn2 or Ni3Sn4). We report here some initial results from a detailed electron microscopic analysis of the microstructures of a commercial (En30A) Ni–Cr steel and a special laboratory made steel (BE 10) having similar Ni and Cr contents, but doped specifically with tin. The composition of the two steels is presented in Table 1. Both steels were oil quenched from 950°C, tempered for 1 h at 650°C and aged at 500°C for times up to 5,000 h. Carbon extraction replicas, taken from polished surfaces were examined in a Philips EM400 microscope fitted with an energy dispersive X-ray system. Selected individual precipitate particles were analysed using convergent beam microdiffraction and X-ray analysis. Attention was focused on the particles which delineated the lath packet and previous austenite boundaries, that is, high-angle boundaries.
Solute segregation and intergranular fracture in steels: a status report☆
Abstract A great deal of progress has been made recently in the understanding of impurity-induced intergranular embrittlement of alloy steels. A technique has been developed for calculating the transition temperature as a function of the hardness and grain size of the steel and the Auger peak height ratio due to metalloid elements, measured on a partly intergranular fracture surface. The effects of most of the major alloy elements on impurity segregation are now understood, as are the effects of heat treatments which allow the formation of alloy carbides. The effects of antimony and tin segregation on intergranular strength have been measured directly by a newly developed method. The problems remaining before an atomistic understanding of the embrittlement mechanism can be achieved are discussed. These include the calculation of the cohesive energy of iron as a function of the solute concentration, and modeling of the dislocation emission at the tip of a propagating brittle crack.
Intergranular fracture in steels
Abstract There seems to be a sufficient basis of experimental evidence to entertain and test the hypothesis that most, if not all, intergranular fractures observed in commercially-produced alloy steels are a result of the accumulation of one or more of Groups IVB to VIB elements in the grain boundaries. Future progress in the understanding of these effects probably will be accelerated if they are treated as components of a generic set, and if studies of complex steels are closely related to experiments on simpler alloys aimed at discovering the underlying physics and chemistry of interfacial embrittlement.