Mathematical Modeling of the Concentrated Energy Flow Effect on Metallic Materials

Numerous processes take place in materials under the action of concentrated energy flows. The most important ones include heating together with the temperature misdistribution throughout the depth, probable vaporization on the surface layer, melting to a definite depth, and hydrodynamic flotation; generation of thermo-elastic waves; dissolution of heterogeneous matrix particles; and formation of nanolayers. The heat-based model is presented in an enthalpy statement involving changes in the boundary conditions, which makes it possible to consider melting and vaporization on the material surface. As a result, a linear dependence of penetration depth vs. energy density has been derived. The model of thermo-elastic wave generation is based on the system of equations on the uncoupled one-dimensional problem of dynamic thermo-elasticity for a layer with the finite thickness. This problem was solved analytically by the symbolic method. It has been revealed for the first time that the generated stress pulse comprises tension and compression zones, which are caused by increases and decreases in temperature on the boundary. The dissolution of alloying elements is modeled on the example of a titanium-carbon system in the process of electron beam action. The mathematical model is proposed to describe it, and a procedure is suggested to solve the problem of carbon distribution in titanium carbide and liquid titanium-carbide solution in terms of the state diagram and temperature changes caused by phase transitions. Carbon concentration vs. spatial values were calculated for various points of time at diverse initial temperatures of the cell. The dependence of carbon particle dissolution on initial temperature and radius of the particle were derived. A hydrodynamic model based on the evolution of Kelvin-Helmholtz instability in shear viscous flows has been proposed to specify the formation of nanostructures in materials subjected to the action of concentrated energy flows. It has been pointed out for the first time that, for certain parameters of the problem, that there are two microand nanoscale peaks in the relation of the decrement to the wavelength of the interface disturbance.


Introduction
At present the flows of concentrated energy find wide application in processing surfaces of various materials [1][2][3][4][5].For instance, low-energy, high-current electron beams with durations up to milliseconds, which is used for strengthening the surface layer [2], smoothing the surface relief [3,5], the process of electron beam impact and exothermic reaction.Diffusion and temperature problems are solved simultaneously in [22,23] in accordance with diverse spatial and temporal scales.This approach is quite complex since it necessitates consideration of heat release in the thermo-conductivity equation.The method stated in combustion theory [24], and applied further in [25,26], was used for consideration of the changing temperature.It relies on the heat-balance equation for a cell on the whole; that is, there is no change in temperature along the spatial value.The first phase of experimental interaction in the system Ti-C and physical and chemical processes taking place in carbon fusion have been investigated [27], and the double-wave structure of wave transformation was proved experimentally.A mathematical model of carbon distribution in titanium carbide and liquid titanium-carbon solution was suggested [28], which, taking into account the diagram of states and phase transitions, result from temperature changes.The authors of this work suggested a framework implying the determination of such process characteristics, which allow the understanding of the controlled process parameters (e.g., energy density of electron beam, pulse duration, pulse repetition, etc.) on the outcomes of experiments.For instance, whether a particle of carbon dissolves in liquid titanium exposed to electron beam.In this case it is quite reasonable to address only to diffusion problem for homogenous temperature field, which can vary over time due to heat of chemical reactions and heat removal.Solution of this problem helps to realize the reason for generation of homogenous titanium layers exposed to heterogeneous plasma flows and processed further by low-energy high-current electron beam [8,9].
Numerous publications emphasize the interest of researchers in development of mathematical models describing nano-structures under the action of concentrated energy flows [29][30][31][32][33][34][35][36][37][38][39].These models are based mainly on computer simulation of processes, going with the development of nano-structural states.The researchers [29,30] speculated that nano-structural state evolves together with the growing hydrodynamic instability in shear-related motion of liquid layers, one of them is viscous.In this case the dispersion equation is considered as a quartic algebraic equation with complex variables.It is rather complicated to analyze the parameters, so decrement vs. wavenumber was assessed numerically.The wavelength agreeing with the peak of the decrement is the most instable; therefore, this wave preserves its length, making its observation possible in the experiment.Two peaks were revealed in decrement vs. wavelength correlation.Approximation of short waves is used in [39], and a simplified dispersion equation is derived.The values of wavelengths were determined for two peaks on the base of this equation.This fact is of significant importance for parameterization of experimental outcomes.This work is focused on derivation and analysis of the dispersion equation for finite layers.

Thermal Model
Let us consider the impact of the electron beam with the surface energy density E S on a flat plate with the thickness l.As we are interested in the distribution of temperature over the depth of the sample, we confine ourselves to solving the one-dimensional problem of thermal conductivity.The x axis is directed inside the plate.The surface x = 0 is affected by the electron current during the period of time t 0 , and there is no heat flow on the back side of the plate x = l.The equation of thermal conductivity is written in an enthalpy statement in order to take into consideration the phase transformations on the boundary: where enthalpy is: where C is specific heat; ρ-density; T-temperature; t-time; λ-thermal conductivity, for which: Here indices S, L, and V refer to solid, liquid, and gas phases; L L and L V are latent heats of melting and vaporization.We suppose ∆T 1 = 100 K; ∆T 2 = 100 K.The solution of Equation ( 1) requires setting initial and boundary conditions.The initial condition is dependent on the constant temperature, which equals to 300 K.
The boundary condition at x = l is written as follows: Mixed boundary conditions at x = 0 are used to take into account the effect of vaporization, and a heat flow is set till the start of vaporization: where t 1 -time when boundary conditions is changed, and it is determined on assumption that the enthalpy on the surface is similar to the vaporization enthalpy at normal pressure, i.e., it results from the equation H(0,t 1 ) = H V .Over the period from t 1 to the completion of the electron beam impact (t 0 ) energy is supplied to the system and consumed for vaporization and emission of the evaporated substance.At these points the enthalpy on the vapor-liquid boundary is constant and equals to the heat of vaporization H V .This boundary moves into the zone of the plate (up to 1 µm), but we disregard this shift and suppose the boundary condition is as follows: As soon as the pulse impact is over, vapor contacts with the plate surface; since the time of vapor emission is several hundreds of microseconds, the temperature of the sample surface is equated to that of vaporization: After completion of the vapor contact with the surface, its temperature can vary in the absence of heat exchange, therefore, the condition of heat exchange is stated as: Thermal and physical characteristics of commercially pure titanium [40][41][42]: T S = 1998 K; L m = 304 kJ/kg; T V = 3560 K; L V = 8900 kJ/kg; ρ S = 4.5 × 10 3 kg/m 3 ; ρ L = 4.1 × 10 3 kg/m 3 ; C S = 318 J/(kg•K); C L = 400 J/(kg•K); λ S = 25 W/(m•K); λ L = 10 W/(m•K).The problem was solved numerically (1)-( 9) for λ L , varying in the range from 20-40 W/(m•K).The coefficient of thermal conductivity of the liquid titanium was selected on assumption that the estimated and experimental values of the penetration depth are concurrent.
To calculate time t 2 we integrate the Equation (1) according to x from zero to l: The Equation (10) we integrate according to time from zero to t 2 : We obtain an expression for each summand in the right part of Equation ( 11): Here x V (t) and x L (t) are computable dependencies of vaporization front coordinates and melting on time, which are given in Figure 1.titanium was selected on assumption that the estimated and experimental values of the penetration depth are concurrent.
To calculate time t2 we integrate the Equation (1) according to х from zero to l: The Equation (10) we integrate according to time from zero to t2: We obtain an expression for each summand in the right part of Equation ( 11): ( , ) Here xV(t) and xL(t) are computable dependencies of vaporization front coordinates and melting on time, which are given in Figure 1.The system is supplied with the energy per a unit of area W(t2) − W(0) = ES; taking into consideration Equations (12).Equation ( 11) is written as follows: The calculations are carried out for E S = 60 J/sm 2 , t 0 = 100 µs.
The system is supplied with the energy per a unit of area W(t 2 ) − W(0) = E S ; taking into consideration Equations (12).Equation (11) is written as follows: On the basis of Equation ( 13) we determine t 2 .The temperature was calculated by means of the implicit first-order difference scheme with respect to time and by the second-order scheme with respect to space.The time increment is 1 µs, and the space increment is 0.1 µm.The obtained algebraic system of equations was solved by the double-sweep method.The thickness of the plate l is set to 600 µm; this quite large thickness can provide results similar to those of an infinitely thick plate over the time, up to 2000 µs [11][12][13][14][15][16][17]40].The depths of penetration in diverse process conditions of electron beam treatment are given in Table 1.It is seen that estimated and experimental values are quite identical.In accordance to the data in Table 1 the dependence of penetration depth on the surface energy density is linear.The processes of vaporization are quite irrelevant at energy density ranging from 10-30 J/cm 2 because temperature on the surface does not reach that of vaporization.As soon as pulse action is completed there is a sharp drop in temperature on the surface, therefore, the penetration depth is small ~10 µm.At Es > 30 J/cm 2 temperature on the surface reaches the temperature of vaporization.A layer of vapor generated over this process creates a heat buffer, as stated above.As a result, temperature on the surface is quite constant from time T = T V to the time when pulse action is completed.This period of time is dependent on energy density.The higher energy density is the longer temperature on the surface is constant.As a consequence, penetration depth increases.The derived dependence of penetration depth on energy density can provide a basis for choosing proper modes of low-energy high-current electron beam treatment.

Model of Thermoelastic Waves Generation
Generation of the thermoelastic waves is a principal problem to be solved for modelling the processes caused by the concentrated energy flows.An attempt to model a thermal situation relying on heat transfer from the inner heat source and generation of thermoelastic waves has been made in [18][19][20]43], where the bipolarity of the thermoelastic wave was modeled numerically.However, the mechanism of origination, that is, the relationship arising from compression and tension to the zones of heating and cooling was not identified.
In this paper the causes and the mechanism of bipolar thermoelastic wave generation were revealed on the basis of an analytical solution of the thermoelastic problem for the layer with a finite thickness when heating the surface, the stress states close to the back and front surfaces were determined as well.
We consider the problem of thermal stresses for a stress-free flat sample with the thickness, which is subject to the heat flow impact.We set thermal conditions as temperature heating.The axis is Metals 2017, 7, 4 7 of 18 perpendicular to the surface of the sample; the other two axes are in the plane of energy flow impact.The plane is referred to as a front surface, and the plane is a back one.We assume that the energy flow is homogenous in the cross-section, therefore, one-dimensional statement of problem is selected, that is, all functions are dependent on the only one spatial variable, where we consider the one-axial stress-strain state with non-zero components of the strain tensors.To state the mathematical problem we use the equations of motion and thermal conductivity, as well as the Duhamel-Neumann relation, the so called dynamic problem of the disconnected thermo-elastisity [31]: Here, ρ, χ are the density and thermal diffusivity of the material, c = (2µ + λ)/ρ is the rate of longitudinal wave propagation, γ = (3λ + 2µ)α t is the coefficient of the thermoelastic coupling, λ, µ are the Lame coefficients, α t is the coefficient of linear expansion, u = u(t,x) is the component of the displacement vector, and T = T(t,x) is the temperature distribution.
A thermal situation at the front surface under the action of energy flows can be written as temperature heating: We set Ψ 0 (t) as a trapezoid.In this case the surface temperature increases in the range from zero to T 0 over the period of time t 1 , it is constant for the period of time t 2 , and goes down from T 0 to zero over the period of time t 3 .The right part Equation ( 15) is written as follows: where H(t) is the Heaviside step function.
In Equation ( 15) the initial conditions are generalized by taking Equation ( 16) into consideration, and the following problems are solved for these conditions: at l 0 = ∞: Danilevskaya problem-momentary growth of temperature (t 1 = 0, t 2 = ∞, t 3 = 0), the problem with the finite time of temperature increase up to the certain value (t 1 -finite, t 2 = ∞), and the case of the increase and decline of temperature over the same time (t 1 = t 3 , t 2 = 0) [44].
Without any regard to the energy flow we assume that a sample is not fixed in the plane of the flow action.The boundary conditions for the stress equal to zero: The initial conditions of the problem: The stated problem has two typical spatial scales: dynamic, equal to the thickness of the sample l 0 = ~1 mm, and thermal-l T = ~10 µm.Therefore, the equation of dynamics is considered in the range from zero to l 0 , whereas the equation of thermal conductivity is considered on the semi-finite line with a zero temperature at infinity.
Metals 2017, 7, 4 8 of 18 The non-dimensional variables are set according to formulae: To solve the problem Equation ( 19) the Laplace transform is used.For the images a system of differential equations is written with the corresponding boundary conditions: where b 2 = αp and Ψ 0 (p) is the Laplace transform of the function Ψ 0 (τ) set according to Equation ( 16).
The solution of the problem Equation ( 21) is written as follows: where: The first summand in Equation ( 23) is an image of the stress in the wave, generated via temperature heating, and the second summand represents the superposition of the straight wave and the wave reflected from the back and front surfaces: The expression below is obtained according to the sum of infinite geometric sequence formula: The second summand in Equation ( 25) describes the waves moving from the back surface to the front one (backward waves), and the third summand in Equation ( 25) is for forward waves.We calculate the stress originals: The designations are used here: Metals 2017, 7, 4 9 of 18 The obtained Equations ( 27) and ( 28) are in line with those written for a semi-finite layer, Equation ( 28) confirms the formula given in [45].Using the theorem of multiplication of originals we obtain the images for the forward and backward waves: The designation used here is: The results of stress distribution computation according to the coordinate for different instants of time are depicted in Figure 2a,b.This distribution makes it evident that the thermoelastic wave is a bipolar one and zones of pressure and extension are located symmetrically (Figure 2a).Provided that temperature heating is a non-symmetrical one, zones of pressure and extension will be distributed non-symmetrically, too.When the wave approaches the back surface, reflection occurs: the zone of pressure in an incident wave is compensated by the reflected tensile wave; the stress is equal to zero for the instant of time up to 1.2 (0.17 µs), if the distance from the back surface does not exceed 0.2 (120 µm) (Figure 2b, curve 2).From the instant of time 1.1 the reflected tensile wave is added to the zone of extension in an incident wave and, as a consequence, tension gets doubled (Figure 2b, curve 1).Splitting off arises because of such an increase of stresses.A detailed investigation of the zone, where splitting off arises, preconditions taking into consideration the period of active tensile stresses and application of the time strength model.Therefore, it is a separate problem to detect the place of splitting off.The obtained Equations ( 27) and ( 28) are in line with those written for a semi-finite layer, Equation ( 28) confirms the formula given in [45].Using the theorem of multiplication of originals we obtain the images for the forward and backward waves: The designation used here is: The results of stress distribution computation according to the coordinate for different instants of time are depicted in Figure 2a,b.This distribution makes it evident that the thermoelastic wave is a bipolar one and zones of pressure and extension are located symmetrically (Figure 2а).Provided that temperature heating is a non-symmetrical one, zones of pressure and extension will be distributed non-symmetrically, too.When the wave approaches the back surface, reflection occurs: the zone of pressure in an incident wave is compensated by the reflected tensile wave; the stress is equal to zero for the instant of time up to 1.2 (0.17 μs), if the distance from the back surface does not exceed 0.2 (120 µ m) (Figure 2b, curve 2).From the instant of time 1.1 the reflected tensile wave is added to the zone of extension in an incident wave and, as a consequence, tension gets doubled (Figure 2b, curve 1).Splitting off arises because of such an increase of stresses.A detailed investigation of the zone, where splitting off arises, preconditions taking into consideration the period of active tensile stresses and application of the time strength model.Therefore, it is a separate problem to detect the place of splitting off.At the instant of time τ = 1.4 (0.2 µs) the wave turns completely around and moves to the face, where it is reflected; the maximum tensile stresses are recorded at the definite distance (up to 150 µm, approximately) (Figure 2b, curve 2).It facilitates, however, strengthening processes, associated with microhardness peak.In experiments, carried out in [46], microhardness peak occurs at the depth of Metals 2017, 7, 4 10 of 18 about 50-100 µm from the face of thin plates.As experimental and estimated values agree with each other, the selected model can be considered a constituent one.
Hence, bipolarity of the thermoelastic wave is the result of change in heating and cooling modes, according to the solution of decoupled thermoelastic problem and parabolic equation of thermal conductivity for the set triangle temperature profile on the surface.The zones of doubled tension have been revealed at the back surface, as well as those of doubled pressure at the face.The developed stress field facilitates rearrangement of defect structure of material, as the consequence, furthers accelerated mass transfer.This fact can help to account for the fact, why the depth of the strengthened layer is increased more than that of thermal impact.
The obtained results can be used for discuss probable mechanisms how to improve mechanical properties of materials at the depth exceeding dimensions of the zone affected by plasma flows.

The Diffusion Model of Dissolution Refractory Inclusions in Metals under Concentrated Flows of Energy Action
Let us consider the dissolution of a high-melting element in liquid titanium, taking carbon as an example.A mathematical model and a method to solve the problem of carbon distribution in titanium carbide and in liquid titanium and carbon solution are considered in terms of the state diagram and temperature changes caused by phase transitions and heat exchange with the ambient environment.The dependence of temperature of the surrounding cell environment with respect to time is the key feature of this model.This problem can be reduced to a non-autonomous singular differential second-degree equation, but it is difficult to analyze it in terms of quality [21,26,47].Therefore, a numerical method is selected to investigate some definite models with particular parameters.
In the model below a cell is considered, which contains a r 0 size carbon particle, placed into liquid titanium with a definite volume of R 0 size.On the C-Ti interface a chemical reaction takes place, as the result of which titanium carbide generates and heat releases.A wave of titanium carbide generation with the coordinate r 1 (t) starts spreading towards carbon.Carbon, which is diffusing through the layer TiC, reacts with titanium, as the result, carbide is generated, therefore, front r 2 (t) is moving.Carbon also dissolves in liquid titanium.Hence, a three-layer structure is generated in the cell: hard carbon-0 < r < r 1 , titanium carbide-r 1 < r < r 2 , carbon solution in liquid titanium-r 2 < r < R 0 .If temperature is assumed to be constant, mathematical statement of the diffusive problem contains the level of diffusion, edge, and initial conditions.Let us consider T e < T < T m in more detail: here T e , T m are the temperatures of eutectic titanium-titanium carbide and titanium carbide-graphite.
Equations of diffusion (sphere-n = 2, cylinder-n = 1, flat plate-n = 0) are as follows: Edge conditions on the extremities of the interval: Conditions to determine the coordinates of boundaries: , r 2 (0) = r 0 (34) Initial conditions: Metals 2017, 7, 4 11 of 18 Here c V = V C /(V C + V Ti )is the inclusion volume fraction of carbon in phases, which depends on the spatial values r and time t; V J are the volumes of corresponding pure components (J = C, Ti). Figure 3 shows the graph of atomic fraction c = N C /(N C + N Ti ) dependent on the coordinate.Atomic fracture can be used to determine the chemical formulae of phases.However, equations of diffusion are written for inclusion volume fractions or mass fractions, mole or atomic concentrations, which are proportional to them.Atomic-inclusion volume fraction conversion and vice versa are described in Equation ( 36): To calculate the temperature in the cell we use the heat-balance equation: Here (i = 1, 2).C 0 is the mean molar capacity of the cell, ν 1 , ν 2 , ν 0 are values, proportional to the moles of carbon in titanium carbide and in solution, as well as to the total mole concentration at the initial instant of time, the proportionality factor is similar.Q i is the molar heat of titanium carbide generation and carbon dissolution in liquid titanium, respectively; and c V is the bulk concentration of carbon in titanium carbide or in solution, c V0 = (r 0 /R 0 ) n+1 is the initial bulk concentration of carbon in the system, ρ J and µ J are the density and molar mass of the component J (J = C, Ti), a is the coefficient of heat exchange, T is the temperature of the cell, and T a is the ambient temperature.We admit that the dependence of ambient temperature on time is pre-set.
The stated mathematical problem Equations ( 32)-( 37) are solved numerically by the method of scalar marching.Time is assumed to be discrete at the moments t n = kτ, τ is the time interval of discretization, and k is the time step number.Let us consider the values c k V , r k 1 , r k 2 , T k to be known for the k time step, we calculate the values for k + 1 time step.An initial-boundary value problem is numerically solved with edge conditions and coefficients of diffusion, taken from k time step.
Ambient temperature was decreasing according to the linear law T a = T 00 − β t.Here β is the rate of cooling.Parameters T 00 , α, and β were varied.Initial temperature was selected equal to T 00 .This approach helped to analyze whether carbon could dissolve in titanium, to determine its dissolution time according to initial temperature and the rate of cooling.
Figures 3 and 4 show the results of calculations when the rate of cooling is equal to zero and there is no heat exchange.Values for r 0 were selected equal to either 10 µm or 10 nm.This was done to compare the time of carbon dissolution under conditions of various scales of cells.
The thickness of titanium carbide layer increases first, then it gets smaller (Figure 3).The time of dissolution is getting reduced as the initial temperature grows (Figure 4a,b).Here, if initial thickness of graphite layer reduces from 10 µm to 10 nm, time of dissolution decreases 10 6 times.The time of graphite dissolution is on the order of microseconds; this conforms to the experiments on the electron-beam treatment of the surface after electro-explosive doping [10].
approach helped to analyze whether carbon could dissolve in titanium, to determine its dissolution time according to initial temperature and the rate of cooling.
Figures 3 and 4 show the results of calculations when the rate of cooling is equal to zero and there is no heat exchange.Values for r0 were selected equal to either 10 µ m or 10 nm.This was done to compare the time of carbon dissolution under conditions of various scales of cells.The thickness of titanium carbide layer increases first, then it gets smaller (Figure 3).The time of dissolution is getting reduced as the initial temperature grows (Figure 4a,b).Here, if initial thickness of graphite layer reduces from 10 µ m to 10 nm, time of dissolution decreases 10 6 times.The time of graphite dissolution is on the order of microseconds; this conforms to the experiments on the electron-beam treatment of the surface after electro-explosive doping [10].Therefore, the submitted model and calculations made on its ground, made it possible to demonstrate that micrometer-order carbon particles dissolve for about 10 s.This time goes far beyond the time of impact on material by concentrated flow of energy.If the dimensions of the particles are of nanometer-order ones, the time of dissolution gets equal to 10 μs in order of magnitude.In this case carbon particle can be dissolved as long as it is treated by electron-beam.We to compare the time of carbon dissolution under conditions of various scales of cells.The thickness of titanium carbide layer increases first, then it gets smaller (Figure 3).The time of dissolution is getting reduced as the initial temperature grows (Figure 4a,b).Here, if initial thickness of graphite layer reduces from 10 µ m to 10 nm, time of dissolution decreases 10 6 times.The time of graphite dissolution is on the order of microseconds; this conforms to the experiments on the electron-beam treatment of the surface after electro-explosive doping [10].Therefore, the submitted model and calculations made on its ground, made it possible to demonstrate that micrometer-order carbon particles dissolve for about 10 s.This time goes far beyond the time of impact on material by concentrated flow of energy.If the dimensions of the particles are of nanometer-order ones, the time of dissolution gets equal to 10 μs in order of magnitude.In this case carbon particle can be dissolved as long as it is treated by electron-beam.We Therefore, the submitted model and calculations made on its ground, made it possible to demonstrate that micrometer-order carbon particles dissolve for about 10 s.This time goes far beyond the time of impact on material by concentrated flow of energy.If the dimensions of the particles are of nanometer-order ones, the time of dissolution gets equal to 10 µs in order of magnitude.In this case carbon particle can be dissolved as long as it is treated by electron-beam.We can say that the process of combined treatment requires for carbon-graphite fibers, micro-fibrille diameter of them is about tens of nanometers.

Modeling of Subsurface Nanostructure Formation
The research into the impact of the electric conductor, explosive-produced, heterogeneous plasma flows on the structure and properties of materials has demonstrated that a multi-layer gradient structure forms at a distance from the treated surface (Figure 5).The first ~1-µm thick nano-structural layer (I) reacts with plasma of incident flow [49].The dimensions of vertically-located cells in the second layer (II) with the structure of cellular-type crystallization are much larger than those located horizontally.The third layer (III) has approximately equal longitudinal and crosscut dimensions of the grain.The forth inner nano-structural layer (IV) is ~1 µm thick.These experimental facts, two nano-structural layers in particular, have become the issue of theoretical investigations.The external nano-layer is possible to account for the significant heat removal and, as a consequence, for the high rate of cooling.However, specific conditions are necessary Metals 2017, 7, 4 13 of 18 in order to obtain such significant rates of cooling, which is hardly ever possible.The internal nano-layer could not be modeled in the thermal model.Moreover, this layer was considered an artifact.Nevertheless, in products hardened quickly from the melt on a rapidly-moving disk (hardening by spinning) there are four structural zones, described in [50].The zone located near to the surface to be hardened, or the zone of freezing, has a fine, disperse structure.It is thought to be generated as the result of multiple-crystal nucleation.The second zone is one of columnar crystal-highly extended grains.A dendrite or dendrite-cellular structure is formed in the third zone.The fourth zone is one of equiaxed randomly-oriented nano-grains.The situation here is much aike that one described above-an internal nano-layer arises under the action of heterogeneous plasma.Furthermore, nano-dimensional structures, which form under significant plastic deformations, arise, if two materials are sheared.Nanostructures were detected in shear bands, when detailed microscopic research was carried out [29].The aforementioned experimental data emphasizes nanostructures to appear often in shear flows.
In [51] one explains why the first nano-structural layer arises involving the mechanism of Kelvin-Helmholtz instability [30] in the nano-dimensional range of wavelengths in conditions of tangentiall-flowing plasma and a layer of molten metal.If two media are moving relative to each other, waves appear (like ripples on water's surface when it is windy).A dispersion evolution is obtained in linear approximation of the evolving boundary surface which is, as a rule, a transcendental algebraic equation attributing increments to the wavelength.This depends on a number of parameters; hence, analytical parameterization can rarely be accomplished.Therefore, a dispersion equation is solved numerically to obtain the dependence of the decrement on the wavelength for definite values of parameters.
The research into the impact of the electric conductor, explosive-produced, heterogeneous plasma flows on the structure and properties of materials has demonstrated that a multi-layer gradient structure forms at a distance from the treated surface (Figure 5).The first ~1-µ m thick nano-structural layer (I) reacts with plasma of incident flow [49].The dimensions of vertically-located cells in the second layer (II) with the structure of cellular-type crystallization are much larger than those located horizontally.The third layer (III) has approximately equal longitudinal and crosscut dimensions of the grain.The forth inner nano-structural layer (IV) is ~1 µ m thick.These experimental facts, two nano-structural layers in particular, have become the issue of theoretical investigations.The external nano-layer is possible to account for the significant heat removal and, as a consequence, for the high rate of cooling.However, specific conditions are necessary in order to obtain such significant rates of cooling, which is hardly ever possible.The internal nano-layer could not be modeled in the thermal model.Moreover, this layer was considered an artifact.Nevertheless, in products hardened quickly from the melt on a rapidly-moving disk (hardening by spinning) there are four structural zones, described in [50].The zone located near to the surface to be hardened, or the zone of freezing, has a fine, disperse structure.It is thought to be generated as the result of multiple-crystal nucleation.The second zone is one of columnar crystal-highly extended grains.A dendrite or dendrite-cellular structure is formed in the third zone.The fourth zone is one of equiaxed randomly-oriented nano-grains.The situation here is much aike that one described above-an internal nano-layer arises under the action of heterogeneous plasma.Furthermore, nano-dimensional structures, which form under significant plastic deformations, arise, if two materials are sheared.Nanostructures were detected in shear bands, when detailed microscopic research was carried out [29].The aforementioned experimental data emphasizes nanostructures to appear often in shear flows.
In [51] one explains why the first nano-structural layer arises involving the mechanism of Kelvin-Helmholtz instability [30] in the nano-dimensional range of wavelengths in conditions of tangentiall-flowing plasma and a layer of molten metal.If two media are moving relative to each other, waves appear (like ripples on water's surface when it is windy).A dispersion evolution is obtained in linear approximation of the evolving boundary surface which is, as a rule, a transcendental algebraic equation attributing increments to the wavelength.This depends on a number of parameters; hence, analytical parameterization can rarely be accomplished.Therefore, a dispersion equation is solved numerically to obtain the dependence of the decrement on the wavelength for definite values of parameters.The maximums in this dependence are obtained at particular wavelengths λ max under conditions of positive increments.Hence, ~λmax -dimensioned waves, and vortices generated by them, are developed, and waves of other lengths, other scales, respectively, cannot be formed.This approach is a conventional one for investigations into instabilities.The idea of using this mechanism to explain the generation of the second internal nano-layer (zone IV) was offered and elaborated in [30].In this work the following dispersion relation is obtained in the approximation of viscous and viscous-potential fluid in terms of Navier-Stokes and Euler equations.
To derive a dispersion equation we deal with a double-layer incompressible liquid (Figure 6), like in [30].The underlayer is assumed to be fixed and viscous.The upper layer is modeled as a perfect liquid moving at speed u 0 parallel to the underlayer.For each layer Navier-Stocks and Euler linearized equations are written: where , and ν 1 is the viscosity on the boundary of layers.We consider cases when the underlayer is viscous or viscous-potential liquid.In the first case ν 1 = ν, so Equation ( 42) is written as follows: For viscous-potential liquid ν = 0 and ν 1 = 0, so Equation ( 42) is written: The analysis of this relation has demonstrated that increment dependencies on the wavelength for viscous and viscous-potential liquids are nearly the same in the wide range of parameters (Figure 7).Therefore, a less complicated dispersion equation of viscous-potential liquid can be applied to analysis in terms of the quality of Kelvin-Helmholtz instability of a perfect and viscous liquid boundary.Numerical computations of increment dependencies on the wavelength at definite values of parameters, which are like those of internal nano-layer formations under the action of heterogeneous plasma flows on ferrum, have revealed that two maximums in the increment-wavelength dependence-in the micro-and nano-range-are possible, if a moving layer is thin (ρ 1 = ρ 2 = 6.3 × 10 3 kg/m 3 , ν = 6 × 10 −7 m 2 /s, σ 0 = 1.2 N/m [52], h = 10 −6 m, H = 10 −6 m, u 0 = 30 m/s).This conforms to the development of two-mode instability.
The microwave mode corresponds with the interaction of perfect liquid layers.The nano-wave mode is formed due to viscosity.In general, the offered interpretation has the following results.In H = h = 1-µm thick layers, if the rates exceed 40 m/s, λ = 1-µm long waves arise; for these values of layer thickness and wavelength the wave can be considered as a moving H c ≈ 10-nm thick boundary layer, where a nano-wave mode is developing; the wavelength is λ c = 100 nm.

Conclusions
1.A thermal mathematical model, which considers vaporization from the surface of the material, has been presented.The dependence of penetration depth vs. energy surface density is obtained.Its linear character has been shown.When comparing penetration depths determined computationally with the experimental data their satisfactory fit has been determined.The period of vaporization has been determined without solving the gas-dynamic problem.2. The mechanism of bipolar thermo-elastic wave generation has been revealed on the basis of being solved analytically, not on the basis of the uncoupled thermo-elasticity problem.The matter of it is that tension and compression in the thermo-elastic wave are caused by an increase and a subsequent drop of temperature on the edge.3. A model of the dissolution of carbon particles in titanium has been analyzed under the action of electron beams.It has been stated that micrometer-dimensional carbon particles get dissolved for about 10 s.This time significantly exceeds the time of concentrated energy flow impact on the material.If particles are nanometer-dimensional ones, the time of dissolution is 10 µs in order of magnitude.In this case carbon particles get dissolved as long as they are impacted by electron beams.4. Formation of internal nano-structural layers has been analyzed under the action of heterogeneous plasma flows.Instability increment dependence on the wavelength with two maximums-in nano-and micro-ranges-have been developed.

Figure 1 .
Figure 1.The temperature dependence of coordinates on time t 1 = 31 µs.Here are x V (t) and x L (t).The calculations are carried out for E S = 60 J/sm 2 , t 0 = 100 µs.

Figure 2 .
Figure 2. The dependence of stress on the coordinates: in the instants of non-dimensional time: (а) 0.21; and (b) 0.41.

Figure 2 .
Figure 2. The dependence of stress on the coordinates: in the instants of non-dimensional time: (a) 0.21; and (b) 0.41.

Figure 5 .
Figure 5.The arrangement of four structural zones.

Figure 5 .
Figure 5.The arrangement of four structural zones.

4 . Conclusions 1 .
A thermal mathematical model, which considers vaporization from the surface of the material, has been presented.The dependence of penetration depth vs. energy surface density is obtained.Its linear character has been shown.When comparing penetration depths determined computationally with the experimental data their satisfactory fit has been determined.The period of vaporization has been determined without solving the gas-dynamic problem.

Table 1 .
The dependence of penetration depth on energy density.