Structural-Phase State, Mechanical Properties, Acoustic and Magnetic Characteristics in the Sustainable Deformation Localization Zones of Power Equipment Made of Structural and Heat Resistant Steels

: The paper presents the results of the analysis of the microstructure, mechanical properties, acoustic and magnetic characteristics of the metal of pipelines that are part of heat and power equipment, after long-term operation, made of structural and heat-resistant steels in the zones of localization of plastic deformation. Samples of 0.2 C steel and 0.12C-1Cr-1Mo-1V steel were studied in the initial state, as well as after operation for 219 and 360 thousand hours, respectively. As a result of the studies carried out for each sample, the phase composition was determined (qualitatively and quantitatively), and the following parameters of the ﬁne structure were calculated: volume fractions of structural components of steel (pearlite and ferrite), scalar ρ and excess ρ ± dislocation density, curvature-torsion of the crystal lattice χ , amplitude of internal stresses (shear stress and long-range stresses). All quantitative parameters of the structure are determined both in each structural component of steel, and in general for each sample. The structure of the metal of all specimens after deformation before the formation of zones of stable localization of deformations consists of a ferrite-pearlite mixture, and for specimens after operation before fracture only of unfragmented and fragmented ferrite. Ferrite, which occupies the bulk of the material, is present both unfragmented and fragmented. For all samples, the ratios ρ ≥ ρ ± , χ = χ pl , σ L ≥ σ d were calculated, which indicate whether there is a danger of the initiation of microcracks in metal samples. For specimens without operation and after operation without damage in zones of stable localization of deformations, these conditions are met, and for specimens after operation until destruction, they are not met. It was found that the structural-phase state in the zones of localization of deformations has a direct effect on the characteristics of non-destructive tests. Thus, for all investigated samples, the values of such parameters as the delay time of the surface acoustic wave, the attenuation coefﬁcient, the amplitude of the received signal, and the intensity of magnetic noise in the zones of deformation localization were established.


Introduction
Organization of protection of the vital interests of the individual and society from accidents at hazardous production facilities is one of the important tasks of modern pro-duction, the achievement of which is impossible without reliable diagnostics of equipment and a reliable assessment of the residual resource [1][2][3][4][5][6][7][8][9][10][11][12].
Complex physicochemical processes occur in the metal of power equipment during long-term operation under the influence of high temperatures and pressure and lead to a change in the structural-phase state, nucleation, accumulation of microdefects and then to the destruction of equipment elements [13][14][15][16][17][18][19].
The amount of equipment that has exhausted its park resource is increasing every year. According to official statistics, 49% of such equipment was installed at the beginning of 2019. However, for certain groups of equipment and enterprises, the figure reached 95%. The largest number of accidents and accidents at hazardous production facilities was found in the Siberian Federal District. The analysis of the causes of accidents and accidents that occurred over the past 5 years when using equipment operating under excess pressure showed that steam and hot water pipelines are one of the most dangerous types of equipment operating under excess pressure, despite the absence of such hazardous factors, as the presence of explosive, fire hazardous and toxic environments [20].
Methods and equipment for non-destructive testing associated with the study of the structural state are currently being developed [21][22][23]. A number of criteria for the limiting state of the base and deposited metal, as well as welded joints, were developed based on the dependences of the characteristics of non-destructive testing methods with quantitative indicators of the structural-phase state [24,25]. However, these criteria require clarification, since associated with the limiting state of the equipment. Increasing the reliability and accuracy of the assessment is impossible without analyzing the structural-phase state and mechanical characteristics of the metal of long-term power equipment. The detection of a characteristic pre-fracture zone or zone of localization of deformations is an important aspect [26]. One of the main advantages of this approach is the fundamental possibility of detecting the site of future destruction of the sample long before necking. In this case, the place of future destruction coincides with the zone of deformation localization. The purpose of this work is to identify deformation localization zones by physical methods of non-destructive testing as the basis for a fundamentally new approach to determining the sites of pre-failure and to assessing the residual life of long-term power equipment.

Materials and Methods
To carry out the stated studies, samples were used that were cut from the drainage pipe of the front screen of a heat power plant without operation, after operation for 219 thousand hours without destruction and for 242 thousand hours before destruction, the material was 0.2 C steel (operating parameters: medium-steam-water mixture, temperature 320 • C and pressure 1.6 MPa). As well as samples from the bend of the steam line before the exhaust valve also without operation, after operation for 260 thousand hours without destruction and for 263 thousand hours before destruction, the material is 0.12C-1Cr-1Mo-1V steel (operating parameters: medium-steam-water mixture, temperature 545-565 • C and pressure 14 MPa.). The chemical composition of the investigated steel is given in Table 1. We used the shape of the samples-"dog-bone" with the dimensions of the working part 40 mm × 6 mm × 2 mm (Figure 1-1). We used the shape of the samples-"dog-bone" with the dimensions of the working part 40 mm × 6 mm × 2 mm (Figure 1-1).

Figure 1.
Schematic representation of sections of pipe zones made of the investigated steels, in which the structure was studied: 1-samples for mechanical tests, 2-conditional zone of localization of deformations; 3-areas for measuring the parameters of non-destructive tests (delay time (R, ns), attenuation coefficient (Katt, 1/μs) and amplitude swing of the received signal (A, 1/mm) of the surface acoustic wave, magnetic noise intensity (MNI, d/q).
The microstructure was analyzed using a Neophot-21 optical microscope (Carl Zeiss Jena, Germany) with a UCMOS03100KPA digital technical video camera, and the mechanical characteristics were determined under uniaxial tension at a constant rate on a Walter + Bai AG LFM-125 testing machine (Walter+Bai AG, Switzerland) at room temperature. The moving speed of the movable gripper was 0.4 mm/min. (quasi-static tests). Simultaneously with stretching, the deformation localization patterns were recorded by the digital image correlation (DIC) method [27,28], which was realized using a PL-B781F video camera (Pixelink, Canada) under illumination with a SNF-xxx-635-30-KB laser. For comparison, the same experiments were performed on similar samples cut from pipes of the same standard sizes that were not in operation (non-operational state).
To study the structure of the metal in the zones of localized deformation, we used the method of transmission electron microscopy (TEM) on thin foils using an EM-125 electron microscope (Sumy electronic devices plant, Ukraine) and an accelerating voltage of 125 kV [29,30]. The working magnification in the microscope column was 25,000 times.
As a result of the studies carried out for each sample, the phase composition was determined (qualitatively and quantitatively), and the following parameters of the fine structure were calculated: volume fractions of structural components of steel, scalar ρ (parameter, that controls changes in dislocation substructures at certain degrees of deformation) and excess ρ± dislocation density, curvature-torsion of the crystal lattice χ, amplitude of internal stresses (shear stress and long-range stresses). All quantitative parameters of the fine structure are determined both in each structural component of steel, and in general for each sample [31][32][33][34].
The samples before and after plastic deformation were tested by non-destructive methods: spectral-acoustic (measuring and computing complex "ASTRON" (designed to measure acoustic characteristics with Rayleigh waves) [20,26]) and magneto-noise methods (structure and stress analyzer "Introscan" (NPF Diagnostics LLC, Belarus) (designed to assess the magnitude of the intensity of magnetic noise) [26]). At the same time, such characteristics as the delay time and velocity of surface acoustic waves, the attenuation coefficient, the amplitude of the received signal, and the intensity of magnetic noise were determined (Figure 1-3). Schematic representation of sections of pipe zones made of the investigated steels, in which the structure was studied: 1-samples for mechanical tests, 2-conditional zone of localization of deformations; 3-areas for measuring the parameters of non-destructive tests (delay time (R, ns), attenuation coefficient (K att , 1/µs) and amplitude swing of the received signal (A, 1/mm) of the surface acoustic wave, magnetic noise intensity (MNI, d/q).
The microstructure was analyzed using a Neophot-21 optical microscope (Carl Zeiss Jena, Germany) with a UCMOS03100KPA digital technical video camera, and the mechanical characteristics were determined under uniaxial tension at a constant rate on a Walter + Bai AG LFM-125 testing machine (Walter+Bai AG, Löhningen, Switzerland) at room temperature. The moving speed of the movable gripper was 0.4 mm/min. (quasistatic tests). Simultaneously with stretching, the deformation localization patterns were recorded by the digital image correlation (DIC) method [27,28], which was realized using a PL-B781F video camera (Pixelink, Canada) under illumination with a SNF-xxx-635-30-KB laser. For comparison, the same experiments were performed on similar samples cut from pipes of the same standard sizes that were not in operation (non-operational state).
To study the structure of the metal in the zones of localized deformation, we used the method of transmission electron microscopy (TEM) on thin foils using an EM-125 electron microscope (Sumy electronic devices plant, Ukraine) and an accelerating voltage of 125 kV [29,30]. The working magnification in the microscope column was 25,000 times.
As a result of the studies carried out for each sample, the phase composition was determined (qualitatively and quantitatively), and the following parameters of the fine structure were calculated: volume fractions of structural components of steel, scalar ρ (parameter, that controls changes in dislocation substructures at certain degrees of deformation) and excess ρ± dislocation density, curvature-torsion of the crystal lattice χ, amplitude of internal stresses (shear stress and long-range stresses). All quantitative parameters of the fine structure are determined both in each structural component of steel, and in general for each sample [31][32][33][34].
The samples before and after plastic deformation were tested by non-destructive methods: spectral-acoustic (measuring and computing complex "ASTRON" (designed to measure acoustic characteristics with Rayleigh waves) [20,26]) and magneto-noise methods (structure and stress analyzer "Introscan" (NPF Diagnostics LLC, Belarus) (designed to assess the magnitude of the intensity of magnetic noise) [26]). At the same time, such characteristics as the delay time and velocity of surface acoustic waves, the attenuation coefficient, the amplitude of the received signal, and the intensity of magnetic noise were determined (Figures 1-3).

Resistant Steels
An analysis of the experimental data showed that long-term operation led to more than a twofold decrease in steel ductility from 22 ± 1.9% to 9.7 ± 1.1% and a significant change in the form of the loading diagram ( Figure 2).
The yield area typical for low-carbon steels is observed in the initial state in the diagram. After operation, it is not observed; therefore, the elastoplastic transition in this state is carried out without the formation of Chernov-Luders bands. Analysis of the results of mechanical tests of samples made of 0.12С-1Сr-1Mo-1V steel showed that long-term operation led to a decrease in the ductility of steel from 30 ± 1.9% to 22 ± 1.1%. At the same time, the strength indicators remained at the same level. The time interval from the beginning of the test to the stable localization of deformation from the state without operation to the fractured state has decreased.
For samples made of 0.12C-1Cr-1Mo-1V steel (Figure 3), the indices a1 and a2 for the state without operation and the state after operation without destruction do not differ significantly and are 0.44 and 0.81, respectively, while for the state after operation and destruction the values indicators a1 and a2 decreased to 0.34 and 0.51, respectively.  Analysis of the results of mechanical tests of samples made of 0.12С-1Сr-1Mo-1V steel showed that long-term operation led to a decrease in the ductility of steel from 30 ± 1.9% to 22 ± 1.1%. At the same time, the strength indicators remained at the same level. The time interval from the beginning of the test to the stable localization of deformation from the state without operation to the fractured state has decreased.
For samples made of 0.12C-1Cr-1Mo-1V steel (Figure 3), the indices a1 and a2 for the state without operation and the state after operation without destruction do not differ significantly and are 0.44 and 0.81, respectively, while for the state after operation and destruction the values indicators a1 and a2 decreased to 0.34 and 0.51, respectively.

Mechanical Test Results of Samples of Power Equipment Made of Structural and Heat Resistant Steels
An analysis of the experimental data showed that long-term operation led to more than a twofold decrease in steel ductility from 22 ± 1.9% to 9.7 ± 1.1% and a significant change in the form of the loading diagram ( Figure 2).
The yield area typical for low-carbon steels is observed in the initial state in the diagram. After operation, it is not observed; therefore, the elastoplastic transition in this state is carried out without the formation of Chernov-Luders bands.
Analysis of the results of mechanical tests of samples made of 0.12C-1Cr-1Mo-1V steel showed that long-term operation led to a decrease in the ductility of steel from 30 ± 1.9% to 22 ± 1.1%. At the same time, the strength indicators remained at the same level. The time interval from the beginning of the test to the stable localization of deformation from the state without operation to the fractured state has decreased.
For samples made of 0.12C-1Cr-1Mo-1V steel (Figure 3), the indices a 1 and a 2 for the state without operation and the state after operation without destruction do not differ significantly and are 0.44 and 0.81, respectively, while for the state after operation and destruction the values indicators a 1 and a 2 decreased to 0.34 and 0.51, respectively.

Structural-Phase State of Samples of Power Equipment Made of Structural and Heat-Resistant Steels before Deformation and in Zones of Stable Localization of Deformation
The matrix of 0.2 C steel is a α-phase-a solid solution of carbon and alloying elements (see Table 1) in α-Fe with a bcc crystal lattice in the initial state. The morphological components of the α-phase are lamellar perlite and ferrite. The volume fraction of lamellar perlite is 85%, ferrite-15% (Figure 4a). Typical images of the ferritic-pearlitic structure are shown in Figure 5.

Structural-Phase State of Samples of Power Equipment Made of Structural and Heat-Resistant Steels before Deformation and in Zones of Stable Localization of Deformation
The matrix of 0.2 С steel is a α-phase-a solid solution of carbon and alloying elements (see Table 1) in α-Fe with a bcc crystal lattice in the initial state. The morphological components of the α-phase are lamellar perlite and ferrite. The volume fraction of lamellar perlite is 85%, ferrite-15% (Figure 4a). Typical images of the ferritic-pearlitic structure are shown in Figure 5. Analysis of the research results showed that the metal matrix of 0.2 С steel sample after operation, but without destruction, is the phase-a solid solution of carbon and alloying elements in α-Fe with a bcc crystal lattice, as well as in the sample of the initial state. Lamellar pearlite and ferrite are also morphological components of the phase. The volume fraction of lamellar pearlite is 85%, ferrite-15%, as in the sample in initial state ( Figure 4b). Typical images of the ferrite-pearlite structure are shown in Figure 6. From Figure 6, it follows that the structure of the metal in the zone of localized deformation of an undisturbed specimen is represented by lamellar pearlite, which is present in the form of unfragmented (also 25%) and fragmented (also 60%), as in the initial state. Ferrite is also presented unfragmented (5%) and partially fragmented (10%). The average value of the size of fragments in pearlite has slightly decreased and is equal to 0.7 μm, in ferrite it has not changed, i.e., is equal to 0.5 μm.   Analysis of the research results showed that the metal matrix of 0.2 C steel sample after operation, but without destruction, is the phase-a solid solution of carbon and alloying elements in α-Fe with a bcc crystal lattice, as well as in the sample of the initial state. Lamellar pearlite and ferrite are also morphological components of the phase. The volume fraction of lamellar pearlite is 85%, ferrite-15%, as in the sample in initial state ( Figure 4b). Typical images of the ferrite-pearlite structure are shown in Figure 6. From Figure 6, it follows that the structure of the metal in the zone of localized deformation of an undisturbed specimen is represented by lamellar pearlite, which is present in the form of unfragmented (also 25%) and fragmented (also 60%), as in the initial state. Ferrite is also presented unfragmented (5%) and partially fragmented (10%). The average value of the size of fragments in pearlite has slightly decreased and is equal to 0.7 µm, in ferrite it has not changed, i.e., is equal to 0.5 µm.  The metal matrix of the 0.2 С steel sample after long-term operation and destruction is also the α-phase-a solid solution of carbon and alloying elements in α-Fe with a bcc crystal lattice, as in the samples of the initial state and in the undisturbed sample. Lamellar pearlite and ferrite are also morphological components of the phase. The volume fraction of lamellar pearlite is also 85%, ferrite-15% ( Figure 4c). The metal matrix of the 0.2 C steel sample after long-term operation and destruction is also the α-phase-a solid solution of carbon and alloying elements in α-Fe with a bcc crystal lattice, as in the samples of the initial state and in the undisturbed sample. Lamellar pearlite and ferrite are also morphological components of the phase. The volume fraction of lamellar pearlite is also 85%, ferrite-15% ( Figure 4c).
Lamellar perlite is also present in the form of unfragmented ( Figure 7) and fragmented. Unfragmented lamellar pearlite is defective and even partially destroyed. Destroyed cementite plates were not detected in the original and undisturbed samples. This is the first difference in the structure of the metal of the destroyed sample. The volume fraction of unfragmented lamellar pearlite is also 25% of the volume of the material. sent as a set of the following structures: (1) dislocation fragments (45%) with an average size of 0.4 μm, inside which cementite particles of a rounded configuration are present on dislocations, along the boundaries of the fragments-lamellar particles of cementite; (2) microcrystalline structure (10%)-micrograins (or dislocation-free fragments), surrounded by cementite interlayers, the average size of which is ~0.2 μm, and (3) nanocrystalline structure (5%) with a dislocation-free grains (fragments) size of 55 nm, at the joints which revealed particles of cementite. All ferrite grains are partially fragmented in the fractured sample compared to the original and non-fractured samples.
The matrix of 0.12С-1Сr-1Mo-1V steel in a state without operation in deformation localization zones is an-phase-a solid solution of carbon and alloying elements in α-Fe with a bcc crystal lattice. The morphological components of the α-phase are pearlite (5%) and ferrite-95% (the fraction of fragmented ferrite is 70%) (Figure 8a). The dislocation substructure in ferrite interlayers is reticulate (Figure 9). Deformation led not only to the destruction of cementite plates, but also to an increase in the scalar dislocation density in ferrite interlayers and further polarization of the dislocation structure. Now the value ρ = 3.43 × 10 10 cm −2 . The amplitude of the curvature-torsion of the ferrite crystal lattice is χ = 560 cm −1 , the excess dislocation density ρ± = 2.24 × 10 10 cm −2 , but the condition ρ > ρ± is preserved in pearlite. Consequently, in the structure of the metal of the sample after prolonged operation and destruction in the zone of localized deformation, fragmented lamellar pearlite is present as a set of the following structures: (1) dislocation fragments (45%) with an average size of 0.4 µm, inside which cementite particles of a rounded configuration are present on dislocations, along the boundaries of the fragments-lamellar particles of cementite; (2) microcrystalline structure (10%)-micrograins (or dislocation-free fragments), surrounded by cementite interlayers, the average size of which is~0.2 µm, and (3) nanocrystalline structure (5%) with a dislocation-free grains (fragments) size of 55 nm, at the joints which revealed particles of cementite.
All ferrite grains are partially fragmented in the fractured sample compared to the original and non-fractured samples.
The matrix of 0.12C-1Cr-1Mo-1V steel in a state without operation in deformation localization zones is an-phase-a solid solution of carbon and alloying elements in α-Fe with a bcc crystal lattice. The morphological components of the α-phase are pearlite (5%) and ferrite-95% (the fraction of fragmented ferrite is 70%) (Figure 8a). The dislocation substructure in ferrite interlayers is reticulate (Figure 9). Deformation led not only to the destruction of cementite plates, but also to an increase in the scalar dislocation density in ferrite interlayers and further polarization of the dislocation structure. Now the value ρ = 3.43 × 10 10 cm −2 . The amplitude of the curvature-torsion of the ferrite crystal lattice is χ = 560 cm −1 , the excess dislocation density ρ ± = 2.24 × 10 10 cm −2 , but the condition ρ > ρ ± is preserved in pearlite. The matrix of 0.12С-1Сr-1Mo-1V steel in the state after operation (260 thousand hours) without destruction, as well as for the state without operation in the zones of localization of deformation, is the phase-a solid solution of carbon and alloying elements in α-Fe with a bcc crystal lattice. The morphological components of the α-phase are pearlite (22%) and ferrite-78% (fragmented ferrite 63%) (Figure 8b). In the zone of localized deformation, pearlite is almost completely destroyed ( Figure 10). The volume fraction of cementite in pearlite grains is 4.8%.   The matrix of 0.12С-1Сr-1Mo-1V steel in the state after operation (260 thousand hours) without destruction, as well as for the state without operation in the zones of localization of deformation, is the phase-a solid solution of carbon and alloying elements in α-Fe with a bcc crystal lattice. The morphological components of the α-phase are pearlite (22%) and ferrite-78% (fragmented ferrite 63%) (Figure 8b). In the zone of localized deformation, pearlite is almost completely destroyed ( Figure 10). The volume fraction of cementite in pearlite grains is 4.8%.  The matrix of 0.12C-1Cr-1Mo-1V steel in the state after operation (260 thousand hours) without destruction, as well as for the state without operation in the zones of localization of deformation, is the phase-a solid solution of carbon and alloying elements in α-Fe with a bcc crystal lattice. The morphological components of the α-phase are pearlite (22%) and ferrite-78% (fragmented ferrite 63%) (Figure 8b). In the zone of localized deformation, pearlite is almost completely destroyed ( Figure 10). The volume fraction of cementite in pearlite grains is 4.8%. The dislocation substructure in ferrite interlayers is mesh. The scalar dislocation density is 3.25 × 10 10 cm −2 . The dislocation structure in pearlite grains is polarized. Amplitude of curvature-torsion χ = 455 cm −1 , excess density of dislocations ρ± = 1.82 × 10 10 cm −2 , i.e., as before, ρ > ρ±. The average amplitude of shear stress σL = 360 MPa, and the average amplitude of long-range (local) stresses has a value of σd = 270 MPa, i.e., also σL > σd. This means that the bending-torsion of the crystal lattice of ferrite in pearlite grains is also created by the dislocation structure and is of a purely plastic nature.
After operation, the structure of 0.12С-1Сr-1Mo-1V steel underwent significant changes: the proportion of the pearlite component decreased significantly, and the average size of pearlite colonies decreased by half. The tendency towards a decrease in the content of pearlite in the destroyed state manifested itself even more clearly. The structure of the steel in this state is a mixture of ferrite with a small content of carbides (Figure 11), the volume fraction of which is 100% (the fraction of fragmented ferrite is 95%) ( Figure  8c).  The dislocation substructure in ferrite interlayers is mesh. The scalar dislocation density is 3.25 × 10 10 cm −2 . The dislocation structure in pearlite grains is polarized. Amplitude of curvature-torsion χ = 455 cm −1 , excess density of dislocations ρ ± = 1.82 × 10 10 cm −2 , i.e., as before, ρ > ρ ± . The average amplitude of shear stress σ L = 360 MPa, and the average amplitude of long-range (local) stresses has a value of σ d = 270 MPa, i.e., also σ L > σ d . This means that the bending-torsion of the crystal lattice of ferrite in pearlite grains is also created by the dislocation structure and is of a purely plastic nature.
After operation, the structure of 0.12C-1Cr-1Mo-1V steel underwent significant changes: the proportion of the pearlite component decreased significantly, and the average size of pearlite colonies decreased by half. The tendency towards a decrease in the content of pearlite in the destroyed state manifested itself even more clearly. The structure of the steel in this state is a mixture of ferrite with a small content of carbides (Figure 11), the volume fraction of which is 100% (the fraction of fragmented ferrite is 95%) (Figure 8c).

Acoustic and Magnetic Characteristics of Metal Samples of Power Equipment Made of Structural and Heat-Resistant Steels before Deformation and in Zones of Stable Deformation Localization
The possibility of cutting metal from an object is not always available during technical diagnostics and industrial safety expertise; therefore, often the only source of information about the state of the metal is non-destructive testing [35][36][37][38]. Currently, control methods are being developed and implemented, the measured characteristics of which are sensitive to changes in structure and mechanical characteristics. One of these methods is the spectralacoustic control method [20][21][22][23]26].
The values of the characteristics of non-destructive testing for specimens of different states of low-carbon steel before deformation varied within: delay time of a surface acoustic wave from 4650 ± 3 ns to 4750 ± 3 ns ( Figure 12a); attenuation coefficient of the surface acoustic wave 0.001 ± 0.002 µs −1 to 0.2 ± 0.003 µs −1 (Figure 12b); the amplitude range of the received signal of the surface acoustic wave is from 387 ± 11 mm −1 to 172 ± 12 mm −1 (Figure 12c) and the intensity of magnetic noise is 290 ± 31 to 350 ± 19 units (Figure 12d). The characteristics of non-destructive tests for all investigated states of specimens made of 0.2 C steel in the zones of localization of deformation had similar values: the delay time of the surface acoustic wave was 4700 ± 3 ns ( Figure 12a); attenuation coefficient of the surface acoustic wave 0.006 ± 0.003 µs −1 (Figure 12b); the amplitude of the received signal of the surface acoustic wave is 227 ± 12 mm −1 (Figure 12c) and the intensity of magnetic noise is 275 ± 31 units (Figure 12d), which indicates the invariability of the characteristics of non-destructive tests in zones of stable localization of deformation. The possibility of cutting metal from an object is not always available during technical diagnostics and industrial safety expertise; therefore, often the only source of information about the state of the metal is non-destructive testing [35][36][37][38]. Currently, control methods are being developed and implemented, the measured characteristics of which are sensitive to changes in structure and mechanical characteristics. One of these methods is the spectral-acoustic control method [20][21][22][23]26].
The values of the characteristics of non-destructive testing for specimens of different states of low-carbon steel before deformation varied within: delay time of a surface acoustic wave from 4650 ± 3 ns to 4750 ± 3 ns ( Figure 12a); attenuation coefficient of the surface acoustic wave 0.001 ± 0.002 μs −1 to 0.2 ± 0.003 μs −1 (Figure 12b); the amplitude range of the received signal of the surface acoustic wave is from 387 ± 11 mm −1 to 172 ± 12 mm −1 ( Figure  12c) and the intensity of magnetic noise is 290 ± 31 to 350 ± 19 units (Figure 12d). The characteristics of non-destructive tests for all investigated states of specimens made of 0.2 С steel in the zones of localization of deformation had similar values: the delay time of the surface acoustic wave was 4700 ± 3 ns ( Figure 12a); attenuation coefficient of the surface acoustic wave 0.006 ± 0.003 μs −1 (Figure 12b); the amplitude of the received signal of the surface acoustic wave is 227 ± 12 mm −1 (Figure 12c) and the intensity of magnetic noise is 275 ± 31 units (Figure 12d), which indicates the invariability of the characteristics of nondestructive tests in zones of stable localization of deformation. Similar results during testing by non-destructive methods were established for samples of heat resistant 0.12С-1Сr-1Mo-1V steel ( Figure 13).

Discussion of the Results of Mechanical Tests of Samples of Power Equipment Made of Structural and Heat-Resistant Steels
Analysis of the mechanical tests results of power equipment samples made of structural steels showed that at the initial stage of loading there is no movement of localized deformation sites, and the plastic flow is formed relatively uniformly throughout the sample volume until a zone of stable deformation localization appears. This zone with an almost constant coordinate is formed before reaching the maximum value of the stress σВ. With further stretching, the magnitude of local deformations in this region increases, while in the rest of the sample volume it practically does not change. Destruction is ultimately realized at a given point in the sample. The time of formation of a stable zone of localization of deformation tloc is correlated with the time of reaching the maximum stress value tB and with the total time of stretching of the specimen before fracture tcrac.
This evolution of deformation localization patterns, which is associated with the appearance of stable deformation localization zones, manifests itself both in the initial state and in any other state, including after prolonged operation. Thus, it is always possible to determine the time of occurrence of tloc, where further necking is formed and destruction occurs, it can always be determined. Table 2 shows the tloc values for all tested samples. So, after long-term operation, the average value of the formation time of a stable localization zone decreased by more than three times in comparison with the initial state.

Discussion of the Results of Mechanical Tests of Samples of Power Equipment Made of Structural and Heat-Resistant Steels
Analysis of the mechanical tests results of power equipment samples made of structural steels showed that at the initial stage of loading there is no movement of localized deformation sites, and the plastic flow is formed relatively uniformly throughout the sample volume until a zone of stable deformation localization appears. This zone with an almost constant coordinate is formed before reaching the maximum value of the stress σ B . With further stretching, the magnitude of local deformations in this region increases, while in the rest of the sample volume it practically does not change. Destruction is ultimately realized at a given point in the sample. The time of formation of a stable zone of localization of deformation t loc is correlated with the time of reaching the maximum stress value t B and with the total time of stretching of the specimen before fracture t crac .
This evolution of deformation localization patterns, which is associated with the appearance of stable deformation localization zones, manifests itself both in the initial state and in any other state, including after prolonged operation. Thus, it is always possible to determine the time of occurrence of t loc , where further necking is formed and destruction occurs, it can always be determined. Table 2 shows the t loc values for all tested samples. So, after long-term operation, the average value of the formation time of a stable localization zone decreased by more than three times in comparison with the initial state. The difference in the time intervals t loc is due to fluctuations in the plasticity for each of the considered states of the studied samples, which is expressed, for example, by the relative elongation before fracture δ. Since loading is carried out at a constant speed v load , then there is a direct relationship between the test time and the deformation of the sample.
where l 0 is the original length of the sample. Then the ratio of the time intervals t loc and t crac -a 1 shows the fraction of uniform deformation from the entire deformation of the material before fracture.
After normalizing for a time t uts that corresponds to the maximum stress σ uts , it is possible to determine the fraction of the homogeneous deformation before the beginning of the falling part of the loading curve a 2 .
It follows from Table 2 that the average values of the parameters a 1 and a 2 differ significantly for the analyzed states of the material. The maximum differences were noted for the parameter a 2 , which also shows the smallest variation in each series of tested samples (0.82 ± 0.06 for the initial state and 0.51 ± 0.11 for the state after use).
The formation of a stable localization zone is associated with the onset of the collapse of the autowave of localized plastic deformation in the framework of the autowave theory of deformation [9][10][11], namely, with the movement of the autowave into the fracture neck. The collapse of an autowave of localized deformation is characterized by the exponents t loc , ε loc , and the parameter a 2 in this work. It can be seen ( Table 2) that in the initial state, the collapse starts much later than in the state after long-term operation. In this case, the duration of the collapse in both states is equal. Thus, uniform deformation of the material in the initial state without the risk of the formation of stress localization zones will be observed even if in the stress concentration areas, the deformation is several percent during stress tests. The maximum deformation value in this case is determined by the parameter a 2 = 0.82. In the state after long-term operation, the parameter a 2 decreased to 0.51, that is, by 40%.
At the same time, individual patterns of the formation of stable localization zones in 0.2 C steel and the conclusions drawn on the basis of these patterns are applicable to 0.12C-1Cr-1Mo-1V steel. For example, the criteria a 1 and a 2 , which characterize the resources of the consumed plasticity before fracture and before the beginning of neck formation, respectively, can be used to assess the resource of long-term operating power equipment.

Discussion of the Results of Studying the Structural-Phase State of Samples of Power Equipment Made of Structural and Heat-Resistant Steels before Deformation and in Zones of Stable Localization of Deformation
Analysis of the microstructure of the samples after deformation until the appearance of stable localization of deformation showed that the greatest changes occurred precisely in these zones of the material under uniaxial tension. It was found that at the initial stage of loading in the exploited metal there is no formation of moving fronts of localized deformation associated with the propagation of Chernov-Luders bands, but long before the appearance of a visible fracture neck, a stable zone of localization of macrostrain appears [39][40][41]. The position of such a zone coincides with the place where further destruction occurs.
Analysis of the results of studies by transmission electron microscopy showed that pearlite and ferrite are distinguished by the presence of a dense dislocation structure. Dislocations fill crystals uniformly, forming curved and mixed lines similar to a threedimensional grid. The average values of the scalar dislocation density (ρ) in each morphological component of the structure, as well as for the material as a whole, are given in Table 3 for the studied samples. Table 3. The magnitude of the scalar density of dislocations in various morphological components of the fine structure and in the whole material (ρ × 10 −10 cm −2 ). It can be seen from Table 3 that when analyzing the transformation of the value of ρ in the zone of localized deformation in the samples in the direction of "initial" → "undestroyed" → "destroyed", a decrease in the value of is traced, although insignificant in all morphological components of the structure, as well as in general material. In addition, the value of ρ is always somewhat less in unfragmented pearlite than in fragmented one. The opposite picture is observed in ferrite.

Sample
A relatively high scalar dislocation density formed in all morphological components of all samples forms internal stresses in the material (shear stresses σ L ). It follows from Table 4 that the values of the σ L amplitudes in all samples are quite similar. However, σ L has a maximum value in the initial sample in all morphological components of the structure. When quantifying such parameters of the metal microstructure of 0.12C-1Cr-1Mo-1V steel samples as the dislocation density (scalar and excess) and the amplitudes of the internal stress fields (tangential and moment) ( Table 5) in the deformation localization zones, the conditions ρ > ρ ± and σ L > σ d , are performed only for the non-operational state. However, they are not carried out in the zones of localization of deformation for states after operation (260 thousand hours) without destruction and after operation (263 thousand hours) and destruction (Table 5). Table 5. Quantitative parameters of the microstructure of the metal of the studied samples of 0.12C-1Cr-1Mo-1V steel in the zone of localization of deformation. Transmission electron microscopy. The general regularity of the formation of deformation localization zones for heatresistant steels is the achievement of critical values of the fragmented substructure, and the identification of deformation localization zones for equipment is justified both for newly commissioned equipment and for equipment in the process of long-term operation.

Discussion of the Results of Measuring the Acoustic and Magnetic Characteristics of the Metal of Samples of Power Equipment Made of Structural and Heat-Resistant Steels before Deformation and in Zones of Stable Localization of Deformation
The nature of the change in the acoustic and magnetic characteristics of non-destructive tests on the surface of the studied samples of structural and heat-resistant steel reveals the fundamental possibility of detecting zones of stable deformation [42] (Figures 14 and 15). steel samples as the dislocation density (scalar and excess) and the amplitudes of the internal stress fields (tangential and moment) (Table 5) in the deformation localization zones, the conditions ρ > ρ± and σL > σd, are performed only for the non-operational state. However, they are not carried out in the zones of localization of deformation for states after operation (260 thousand hours) without destruction and after operation (263 thousand hours) and destruction ( Table 5).
The general regularity of the formation of deformation localization zones for heatresistant steels is the achievement of critical values of the fragmented substructure, and the identification of deformation localization zones for equipment is justified both for newly commissioned equipment and for equipment in the process of long-term operation.

Discussion of the Results of Measuring the Acoustic and Magnetic Characteristics of the Metal of Samples of Power Equipment Made of Structural and Heat-Resistant Steels before Deformation and in Zones of Stable Localization of Deformation
The nature of the change in the acoustic and magnetic characteristics of non-destructive tests on the surface of the studied samples of structural and heat-resistant steel reveals the fundamental possibility of detecting zones of stable deformation [42] (Figures 14 and  15).
Consequently, the possibility of detecting localized deformation zones by spectralacoustic control method in structural and heat-resistant steels is presented.

Statistical Processing of the Results
All research results were statistically processed and the dependences of the parameters of the structural state and mechanical characteristics on the results of non-destructive tests in the metal of samples made of Structural and Heat Resistant Steels, including in the zones of localization of deformations, were plotted.
Thus, with an increase in the amplitude of the moment (long-range) fields of internal stresses (σd, MPa) from 245 to 405 MPa, an increase in the delay time of the surface acoustic wave (R, ns) by 145 ns is observed ( Figure 16). The velocity of propagation of the surface acoustic wave (V, m/s) describes better the change in the value of the curvature-twist of the crystal lattice (χ, cm −1 ) than the attenuation coefficient of the surface acoustic wave (Katt, μs −1 ) ( Figure 17).  Consequently, the possibility of detecting localized deformation zones by spectralacoustic control method in structural and heat-resistant steels is presented.

Statistical Processing of the Results
All research results were statistically processed and the dependences of the parameters of the structural state and mechanical characteristics on the results of non-destructive tests in the metal of samples made of Structural and Heat Resistant Steels, including in the zones of localization of deformations, were plotted.
Thus, with an increase in the amplitude of the moment (long-range) fields of internal stresses (σ d , MPa) from 245 to 405 MPa, an increase in the delay time of the surface acoustic wave (R, ns) by 145 ns is observed ( Figure 16). The velocity of propagation of the surface acoustic wave (V, m/s) describes better the change in the value of the curvature-twist of the crystal lattice (χ, cm −1 ) than the attenuation coefficient of the surface acoustic wave (K att , µs −1 ) ( Figure 17).

Statistical Processing of the Results
All research results were statistically processed and the dependences of the parameters of the structural state and mechanical characteristics on the results of non-destructive tests in the metal of samples made of Structural and Heat Resistant Steels, including in the zones of localization of deformations, were plotted.
Thus, with an increase in the amplitude of the moment (long-range) fields of internal stresses (σd, MPa) from 245 to 405 MPa, an increase in the delay time of the surface acoustic wave (R, ns) by 145 ns is observed ( Figure 16). The velocity of propagation of the surface acoustic wave (V, m/s) describes better the change in the value of the curvature-twist of the crystal lattice (χ, cm −1 ) than the attenuation coefficient of the surface acoustic wave (Katt, μs −1 ) ( Figure 17).   The established dependencies have high values of the correlation coefficient. In the real practice of carrying out diagnostic work during the examination of industrial safety, there is no possibility of deep examination of the metal using electron microscopy methods or the use of speckle photography and digital image correlation during the operation of power equipment. The results of non-destructive tests obtained during equipment shutdowns for control tests and repair and restoration work are one of the possible types of information [43][44][45][46][47][48][49][50][51]. The dependences of structural and deformation indicators on acoustic and magnetic characteristics ( Table 6) were selected using statistical processing of research results based on a comparison of the obtained values of the correlation coefficients for equipment made of low carbon 0.2 C steel and heat resistant 0.12С-1Сr-1Mo-1V steel.  The established dependencies have high values of the correlation coefficient. In the real practice of carrying out diagnostic work during the examination of industrial safety, there is no possibility of deep examination of the metal using electron microscopy methods or the use of speckle photography and digital image correlation during the operation of power equipment. The results of non-destructive tests obtained during equipment shutdowns for control tests and repair and restoration work are one of the possible types of information [43][44][45][46][47][48][49][50][51]. The dependences of structural and deformation indicators on acoustic and magnetic characteristics ( Table 6) were selected using statistical processing of research results based on a comparison of the obtained values of the correlation coefficients for equipment made of low carbon 0.2 C steel and heat resistant 0.12C-1Cr-1Mo-1V steel. Table 6. Dependences of structural and deformation parameters on acoustic and magnetic characteristics.

1.
The studies of the structural-phase state of the metal of the samples were carried out without operation, after operation without destruction and with destruction from structural and heat resistant steels in the zone of stable localization of macrodeformations. A connection between the processes of localization of macrodeformations and the evolution of the substructural state for structural and heat resistant steels is established. On the basis of the presented results and their discussion, on the one hand, it can be argued that information on the localization of macrodeformation, together with the data of the spectral-acoustic method, can be used to assess the residual life of a long-term operating power equipment.

2.
The structure of the metal of all specimens made of structural and heat-resistant steels after deformation before the formation of zones of stable localization of deformations consists of a ferrite-pearlite mixture, and for specimens after operation before fracture only of unfragmented and fragmented ferrite. Ferrite, which occupies the bulk of the material, is present both unfragmented and fragmented. For all samples, the ratios ρ > ρ ± , χ = χ pl , σ L > σ d were calculated, which indicate whether there is a danger of the initiation of microcracks in metal samples. For specimens without operation and after operation without damage in zones of stable localization of deformations, these conditions are met, and for specimens after operation until destruction, they are not met. 3.
The structure of the metal in the zones of localization of deformations directly affects the characteristics of non-destructive tests. The characteristics of non-destructive tests for all investigated states of samples made of structural and heat-resistant steels in the zones of localization of deformation had similar values: the delay time of the surface acoustic wave was 4700 ± 5 ns; attenuation coefficient of the surface acoustic wave 0.006 ± 0.003 µs −1 and 0.004 ± 0.002 µs −1 ; the amplitude range of the received signal of the surface acoustic wave is 227 ± 12 mm −1 and 302 ± 14 mm −1 and the intensity of magnetic noise is 275 ± 31 units and 400 ± 19 units for structural and heat-resistant steels, respectively. The possibility of detecting zones of localized deformation by the spectral-acoustic control method in structural and heat-resistant steels has been found.