Work-hardening of ferrite and microstructure-based modelling of its mechanical behaviour under tension
Introduction
The easiest and most extended approach to predict basic tensile properties of steels with ferrite and ferrite–pearlite microstructures entails a number of empirical equations. One of the most popular expresses the yield stress σy as a function of different strengthening contributions [1], [2], [3], [4], [5], [6]:where σf is the Peierls–Nabarro stress or lattice friction stress, σss and σs are the short-range internal stresses produced, respectively, by interstitial and substitutional elements in solid solution, and σd is the contribution of ferrite grain size d.
It is generally assumed that an element going into solid solution produces an increase in strength proportional to its concentration and independent of the presence of other elements [1]. However, the proportionality constants used to express the particular contribution by the unit weight of each element to σs and σss are subjected to some degree of variation depending on the source [7], [8], [9], [10], [11]. Substitutional elements produce a moderate strengthening effect, as compared to interstitials like carbon and nitrogen, whose contribution is also enhanced by their strong interaction with dislocations [12], [13].
The grain microstructure contribution for polygonal ferrite follows a Hall–Petch relationship [1], [2], [3], [4], [5]:in which σHP and kHP are constants and kHP ≅ 15–18 (MPa mm0.5) when d is expressed as the mean linear intercept [5]. Similar equations can also be found to express tensile strength. However, the stress–strain (σ–ε) curve is required for a number of applications that can be described by simple empirical equations [14], [15], [16], [17], from which the most broadly applied is the Hollomon equation:in which k and n are independent of strain, ε, and can be deduced for ferrite using the following empirical correlations obtained by Morrison at moderate ferrite grain sizes [18]:Similar approaches can also be found that extended these equations to include other effects such as composition [19], [20] and precipitates.
More recently, attempts have been made by various authors to develop alternative formulations based on physical principles [11], [21], [22], [23]. This research investigates the work-hardening of ferrite, and develops a microstructure-based predictive model describing the mechanical behaviour under tension of ultra-low and extra-low carbon steels with different ferrite grain sizes.
Section snippets
Work-hardening models
As reviewed in Ref. [24], the macroscopic flow stress σ and the plastic strain ε are related to the critical resolved shear stress for the current microstructure state τ and to the amount of crystallographic slip γ, via an orientation factor M through:In most cases, the microscopic or intrinsic hardening rate of a crystalline element dτ/dγ can be related to the macroscopic flow stress of a polycrystalline aggregate, according to:with M now being the average orientation
Experimental procedure
Two extra-low carbon steels with similar compositions have been used in the present work together with tensile data obtained from literature for other extra-low and ultra-low carbon steels [18], [22], [32]. The composition and the mean ferrite grain size d, expressed as the mean linear intercept, are given in Table 1 for all these steels. The microstructure of the steels is mainly ferrite with less than 5% pearlite content.
The two as-hot-rolled steels in the present work (E-15 and E-17) have
Application of the model and discussion
The tensile curves from the steels in Table 1 are the basis for the present work. A formulation based on Eq. (8) was previously applied [11], [22] to describe the tensile curves of ferrite, assuming a constant dislocation mean free path L defined by the ferrite grain size. The formulation which considers a mean free path depending on both the grain size and a strain-dependent contribution, due to the instantaneous dislocation density, has recently been applied to different microstructures in
Conclusions
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The analysis of the work-hardening experienced by different extra-low and ultra-low carbon steels when deformed under tension at room temperature shows that stage II work-hardening is not directly observed between yield point elongation and the onset of necking. The work-hardening rate of ferrite decreases with stress (strain), in agreement with the stage III deformation mode. A delayed saturation of the stress is observed for some of the steels.
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A formulation that takes into account a
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