displacement shift complete DSC lattice Auxiliary lattice used for descrip-tion of the atomic structure of high-angle grain boundaries.. Planes of DSC lattice are parallel to the CSL pl
Trang 1dispersion strengthening Strength increase caused by incoherent particles, in
comparison to the matrix phase See Orowan mechanism.
dispersoid See dispersed phase This term frequently relates to inert, e.g., oxide,
particles in dispersion-strengthened alloys or to incoherent precipitates.
dispersoid-free zone Narrow, particle-free zone delineating the grain
bound-aries arranged perpendicular to the principal tensile stress in the sample Such zones occur because of diffusional creep.
displacement cascade Cluster of various point defects, mostly vacancies and
self-interstitials, occurring due to irradiation damage by high-energy (∼1 MeV) ions or thermal neutrons The size of the clusters depends on both
the mass and energy of the primary particles and on the atomic mass in the material irradiated Cascades are characterized by a high concentration
of self-interstitials at the cascade periphery and by an identical concen-tration of vacancies in the cascade core
displacement shift complete (DSC) lattice Auxiliary lattice used for
descrip-tion of the atomic structure of high-angle grain boundaries Planes of DSC lattice are parallel to the CSL planes and pass through all the atomic sites in the crystal lattices of two disoriented grains The shift of the CSL along any translation vector of the DSC lattice changes only the CSL
position, and does not change the CSL itself Thus, these vectors can be
considered to be the Burgers vectors of perfect grain-boundary disloca-tions The minimum length of the vector equals b/Σ, where b is the Burgers vector of primary dislocation, and Σ is a CSL parameter
displacive transformation Name of shear-type transformation used in ceramic
science
divacancy Complex of two vacancies in adjacent lattice sites Divacancy has a
smaller free energy in comparison to two single vacancies far removed
from one another
divorced eutectoid Microconstituent that, in binary systems, is supposed to be
two-phase (see eutectoid colony), but, in fact, is single-phase Such a structure forms when crystallites of the occurring solid phases grow inde -pendently, and crystallites of one of these phases join up with proeutectoid
crystals of the same phase Divorced eutectoid is also observed when the
volume fraction of a phase undergoing eutectoid reaction is low (<5
vol%)
divorced pearlite Divorced eutectoid in steels.
dodecahedral plane {110} plane in cubic structures.
domain structure In ferromagnetic and ferrimagnetic materials, a structure
formed by magnetic domains; in ferroelectrics, it is formed by ferroelec-tric domains Domain structure decreases the energy of magnetic (or electric) poles at the free surface of a body, at the grain boundaries and interfaces, at particles whose size is greater than the domain wall
thick-ness, etc The energy is known as magnetostatic or electrostatic energy, respectively In the absence of an external magnetic (electric) field, domain structure eliminates the poles completely, and the magnetization (polar-ization) vectors of various domains are oriented in such a way that their
Trang 2dispersion strengthening Strength increase caused by incoherent particles, in
comparison to the matrix phase See Orowan mechanism.
dispersoid See dispersed phase This term frequently relates to inert, e.g., oxide,
particles in dispersion-strengthened alloys or to incoherent precipitates.
dispersoid-free zone Narrow, particle-free zone delineating the grain
bound-aries arranged perpendicular to the principal tensile stress in the sample Such zones occur because of diffusional creep.
displacement cascade Cluster of various point defects, mostly vacancies and
self-interstitials, occurring due to irradiation damage by high-energy (∼1 MeV) ions or thermal neutrons The size of the clusters depends on both
the mass and energy of the primary particles and on the atomic mass in the material irradiated Cascades are characterized by a high concentration
of self-interstitials at the cascade periphery and by an identical concen-tration of vacancies in the cascade core
displacement shift complete (DSC) lattice Auxiliary lattice used for
descrip-tion of the atomic structure of high-angle grain boundaries Planes of DSC lattice are parallel to the CSL planes and pass through all the atomic sites in the crystal lattices of two disoriented grains The shift of the CSL along any translation vector of the DSC lattice changes only the CSL
position, and does not change the CSL itself Thus, these vectors can be
considered to be the Burgers vectors of perfect grain-boundary disloca-tions The minimum length of the vector equals b/Σ, where b is the Burgers vector of primary dislocation, and Σ is a CSL parameter
displacive transformation Name of shear-type transformation used in ceramic
science
divacancy Complex of two vacancies in adjacent lattice sites Divacancy has a
smaller free energy in comparison to two single vacancies far removed
from one another
divorced eutectoid Microconstituent that, in binary systems, is supposed to be
two-phase (see eutectoid colony), but, in fact, is single-phase Such a structure forms when crystallites of the occurring solid phases grow inde -pendently, and crystallites of one of these phases join up with proeutectoid
crystals of the same phase Divorced eutectoid is also observed when the
volume fraction of a phase undergoing eutectoid reaction is low (<5
vol%)
divorced pearlite Divorced eutectoid in steels.
dodecahedral plane {110} plane in cubic structures.
domain structure In ferromagnetic and ferrimagnetic materials, a structure
formed by magnetic domains; in ferroelectrics, it is formed by ferroelec-tric domains Domain structure decreases the energy of magnetic (or electric) poles at the free surface of a body, at the grain boundaries and interfaces, at particles whose size is greater than the domain wall
thick-ness, etc The energy is known as magnetostatic or electrostatic energy,
Trang 3ε-carbide Transient phase of an approximate composition Fe2.4C with the hex-agonal crystal structure precipitating in steels from as-quenched marten-site at a low-temperature tempering treatment.
ε-martensite Martensite with HCP crystal structure occurring either at high
external pressures or in some plastically deformed austenitic steels Its occurrence may be connected with the existence of HCP allotropic mod-ification of iron, known as ε-Fe
η-carbide Transient phase of composition Fe2C with orthorhombic crystal
struc-ture; it precipitates in steels from as-quenched martensite at a low-tem-perature tempering treatment (at 50–200°C).
earing Phenomenon revealing itself in the appearance of undulations along the
rim of deep drawn caps and connected with planar anisotropy of the sheet used and, thus, with its crystallographic texture The propensity for earing
can be estimated from the magnitude of ∆r-value.
easy glide Stage of plastic deformation in single crystals wherein only one slip
system is active and the strain hardening rate is low due to a small increase
in dislocation density In crystals with HCP structure, such a stage can
be observed up to relatively high strains In crystals with cubic crystal structure, this stage is either rapidly relieved by multiple slip or is not
observed at all
easy magnetization direction Lattice direction along which the magnetization
energy in ferromagnetic or ferrimagnetic single crystals is minimum In
Fe, it is 〈001〉; in Ni, it is 〈111〉; and in Co, it is 〈0001〉 Magnetization
vectors in magnetic domains lie close to or coincide with the easy
mag-netization direction
edge dislocation Dislocation whose Burgers vector is perpendicular to its line
It can be considered the edge of an extra plane inserted in a crystal lattice
If the extra plane is situated above the slip plane of the dislocation, the
dislocation is assumed positive; in the opposite case, it is assumed nega
tive It should be noted that the dislocation sense is a conventional char
-acteristic
elastic deformation Deformation induced by some external force and
disappear-ing after its removal Elastic deformation can also be associated with
Trang 4face-centered cubic (FCC) structure One of the two most densely packed
crys-tal structures (see Figure F.1) with coordination number 12, atomic
pack-ing factor 0.74, and the close-packed planes {111} and close-packed directions 〈110〉 The radius of tetrahedral void equals 0.225R and that
of octahedral void is 0.415R, where R is the atomic radius In a densely
packed structure, the atoms of each most densely packed layer lie in the hollows of the lower layer In the FCC structure, the atom centers of the
second layer are arranged in the B hollows of the first layer (see
Fig-ure F.2) The atom centers of the third layer are arranged in the hollows
of the second layer and above the C hollows of the first layer The atom
centers of the fourth layer are arranged in the hollows of the third layer
and above the A centers of the first layer Thus, the stacking sequence of
the atom layers {111} in FCC structure can be described as
…ABCABCA….
face-centered lattice Cubic or orthorhombic Bravais lattice wherein, along with
the points at the vertices of the corresponding unit cell, there are additional
points at the centers of all the cell faces
F-center Color center occurring due to electron trapping by a vacancy in a cation
sublattice.
FIGURE F.1 Unit cell of FCC lattice.
FIGURE F.2 Sequence of close-packed planes
{111} in FCC lattice See text
C
B
A
Trang 5γ-Fe Allotropic form of iron having FCC crystal structure and existing between
910° and ∼1400°C at atmospheric pressure
γ ′-phase In Ni alloys, an intermediate phase of composition Ni3(Ti,Al) The
phase has the same FCC lattice as the matrix, γ solid solution, although
the Ti and Al atoms in the γ′-phase lattice occupy cube vertices only, whereas in the γ solid solution, they occupy the lattice sites randomly At
a certain alloy composition, the interface between the γ′- and γ-phases is perfectly coherent, and the precipitates of γ′-phase are stable to coarsen-ing.
garnet ferrite Ferrimagnetic oxide of stoichiometry R3Fe5O12, where R is a trivalent rare-earth element or yttrium
gas constant R = 8.314 J⋅mol–1⋅K–1 = 8.62⋅10–5 eV⋅K–1
general grain boundary High-angle grain boundary whose disorientation
sig-nificantly differs from that of special boundaries In terms of CSL,
dis-orientations at general boundaries are assumed to be characterized by Σ
> 25 The atomic structure of general boundaries is distorted, but is not amorphous; it is not systematically described so far General boundary is also known as random boundary.
geometric coalescence Merging of two adjacent grains of almost the same
ori-entation Since their disorientation is small, they are separated by a sub-boundary, and their coalescence can occur without a significant rotation
of their lattices, as in the case of subgrain coalescence See also grain
coalescence
geometrically necessary dislocations Dislocations contributing to the lattice
curvature inside a grain (subgrain) or to disorientation of a low-angle boundary For instance, consider a grain in which there are only parallel edge dislocations of different sense If the numbers of dislocations of the opposite sense, N+ and N– are the same, geometrically necessary
disloca-tions in the grain are lacking If, however N+ > N– the number of
geomet-rically necessary dislocations equals N+ – N–
Gibbs’ free energy Free energy
G = H – TS