In the first part of this work a comprehensive model of the continuous hardening of 3D-axisymmetric steel components by induction heating has been developed. In the model, the Maxwell and heat flow equations are solved using a mixed numerical formulation : the inductor and the workpiece are enmeshed with finite elements (FE) but boundary elements (BE) are used for the solution of the electromagnetic equations in the ambient air. This method allows the inductor to be moved with respect to the workpiece without any remeshing procedure. The heat flow equation is solved for the workpiece using the same FE mesh. For the thermal boundary conditions, a net radiation method has been implemented to account for grey diffuse bodies and the viewing factors of the element facets are calculated using a "shooting" technique. These calculations have been coupled to a metallurgical model describing the solid state transformations that occur during both heating and cooling. From the local thermal history, the evolution of the various phase fractions are predicted from TTT-diagrams using an additivity principle. A micro-enthalpy method has been implemented in the heat flow calculations in order to account for the latent heat released by the various transformations. At each time step, the local properties of the material, in particular its magnetic permeability, are updated according to the new temperatures and magnetic field. Special attention has been taken for the description of the boundary conditions associated with the water spraying below the inductor. The heat transfer coefficient has been deduced from the inverse modelling of temperatures measured at various locations of a test piece. This preliminary work has been complemented with measurements of the magnetic permeability of the 42CrMo4 steel from which the workpieces are made. This part of the study also includes dilatometric measurements for the verification of the additivity principle used in the simulation. The model has been applied to three cases of increasing complexity : induction stream heating of a steel cylinder without quenching, stream quenching of a steel cylinder and, finally, stream quenching of a non-cylindrical workpiece. The results of the simulation have been compared with experimental cooling curves, microstructures and hardness profiles. In the second part of this work, the phase transformations that occur in hypoeutectoid steels during heating have been investigated at the scale of the microstructure according to a microscopic approach. Several models have been developed in order to describe the various steps of the austenitisation process : (i) pearlite dissolution, (ii) transformation of ferrite into austenite and homogenization, (iii) grain growth in austenite. In a first approach, each step has been modeled separately. The dissolution of pearlite has been described using a two-dimensional finite element model with a deforming mesh and a remeshing procedure. The diffusion equation has been solved in austenite (γ) for a typical domain representative of a periodic structure of ferrite (α) and cementite (θ) lamellae. The α/γ and θ/γ interfaces are allowed to move with respect to the local equilibrium condition, including curvature effects via the Gibbs-Thompson coefficient. The model has been used to predict the concentration field and the shape of the interface at different stages of the pearlite dissolution. Maps representing the steady state dissolution rate as a function of the temperature and lamellae spacing have been obtained for small values of overheating. The appearance of a non-steady state regime at higher temperature has been discussed. The transformation of ferrite into austenite has been described using a pseudo-front tracking finite volume approach for solving the diffusion equation in a 1D, 2D or 3D domain. At the start of the computation, the volume is made of ferritic particles and austenitic zones resulting from the pearlite dissolution. The model allows to calculate the kinetics of the phase transformation as a function of the temperature and the initial microstructure. Although the comparison of the transformation kinetics with experimental results was quite satisfactory, it appeared that the calculated kinetics were slightly slower. This effect has been attributed to the other alloying elements which are contained in the Ck45 steel used for the experiments. This discrepancy has also been explained by a stereological effect which is due to the calculation in a 2D section instead of a 3D domain as demonstrated by a comparison of 2D and 3D simulations. The austenitic grain growth has been described with two models based respectively on a Monte Carlo technique and a mechanical approach. A methodology for obtaining a correspondence between the simulation time scale and real time has been presented and applied to the Ck45 steel. The value of the exponent n of the grain growth law d = Κ t1/n (where d is the mean diameter and t the time) has been determined for both models. The mechanical model (n=2) turned out to describe perfectly the case of normal grain growth as it occurs in liquid-gas systems. However the results of the Monte Carlo simulation (n=2.3) are in better agreement with the non-ideal behaviour of the Ck45 steel. The influence of the impurities and particles which are present in real materials should be taken into account in both models if a more quantitative agreement is to be obtained. Finally, a combined model coupling the various steps of the austenitisation process has been proposed. It allowed to show that the assumption consisting in dividing the process in three separate steps is valid in most cases. This combined model is a first attempt for a comprehensive modelling of the austenitisation process.