Low weight in combination with high strength and good corrosion resistance make titanium alloys excellent candidates for aerospace applications. Their application under conditions where hydrogen is present, e.g., as a fuel component, is limited though, due to their susceptibility to hydrogen embrittlement. [1] While the solubility of hydrogen in a-titanium (hcp) is low and therefore brittle hydrides form rather early, b-titanium (bcc) is relatively insensitive to hydrogen embrittlement because large amounts of hydrogen can be accommodated on interstitial lattice sites. [2] In order to assess the range of practical application conditions for b-titanium alloys in hydrogen bearing environments, it is necessary to study the kinetics and thermodynamics of hydrogen uptake and diffusion in the alloy as well as the effect of hydrogen on the mechanical properties of b-titanium alloys. The experiments reported in this paper have been performed in the framework of these studies. [3,4] Experimental data on the thermodynamics and kinetics of hydrogen uptake in a-titanium alloys are established in the literature, [5,6] experiments on b-titanium alloys are rare though. [7,8] Here, first results on hydrogen uptake and diffusion in three technical b-titanium alloys are being reported. Further, more detailed studies to quantify the effect of heat treatment and alloy microstructure are currently under way.Three technical b-titanium alloys with different stability of the b -phase and the following compositions were chosen for this study to elucidate effects of phase stability and alloy composition: Ti-10V-2Fe-3Al (Ti 10-2-3, near-b titanium alloy), Ti-15MO-2.7Nb-3Al-0.2Si (Ti 21S, metastable b-titanium alloy), and Ti-35V-15Cr (Alloy C, stable b-titanium alloy). The microstructures of these alloys depend on the applied heat treatment. With the exception of Alloy C, which is the only stable b-titanium alloy studied here, both a-and b-phase are present for conditions heat treated below the b-transus. Therefore, the diffusion coefficients determined are apparent diffusion coefficients and depend on the thermal pre-treatment of the alloy. Figure 1 shows SEM micrographs of several alloy microstructures as an example. The microstructure of Ti 10-2-3 in the overaged condition with globular primary a-phase and needle-shaped secondary a-phase in a b-matrix is shown in Fig. 1 (a). The microstructure of Ti 10-2-3 ( Fig. 1 (b)) after a solution-anneal above the b-transus temperature shows secondary a-phase formed during cooling in a b-matrix. Ti 21S after solution-anneal and aging has a basket-weave structure with needle-shaped a-phase in b-matrix ( Fig. 1(c)). Alloy C consists almost entirely of b-phase ( Fig. 1(d)).Kinetics and thermodynamics of hydrogen uptake were determined in the temperature range from 500 to 950 C and for hydrogen partial pressures between 9 and 100 mbar using volumetric measurements. The main part of the volumetric system (Fig. 2) is a bellows with a usable volume of three liters. The hydrogen uptake of the specimen from...