or shaft. The fatigue crack length L (mm) was measured in a given number of loading cycles until the specimen was destroyed. The photos fatigue fracture is presented in Figure 4(b).
3. Results and Discussions
The main structural difference between genuine Damascus steel (Ds15P) and modern carbon Tool steel type У15A is the heterogeneity of the distribution of excess carbides in the troostite matrix. The heterogeneity of the distribution of carbides is inherent in many tool steels, but only in genuine Damascus blades, it has reached its perfection.
Samples for studies of inhomogeneous structure were cut from a fragment of the knife blade in three directions: from the side of the blade butt (longitudinal direction); from the end side of the blade (transverse direction); from the front side of the blade surface (frontal direction).
In the longitudinal direction occurs a heterogeneous layered structure during the forging of the knife blade (Figure 5(a)). On a dark background of the troostite matrix, light layers from 15 µm to 45 µm thick are seen, consisting of with oblong cementite particles. The density of the discontinuous carbide layers ranges from 10 to 15 pieces in 1.0 mm. Thickness troostite layers between the carbide layers is in the range from 45 µm to 75 µm. The hardness of the butt of the blade knife is 48 HRC.
In the transverse direction of the blade knife (the edge of the blade), as in the longitudinal direction (the butt of the blade), there is an inhomogeneous layered structure (Figure 5(b)). Dark areas troostite layers have sizes from 45 µm to 75 µm. Between them, there are strips of oblong carbides of cementite, forming layers with sizes from 20 µm to 40 µm. It is estimated that the inhomogeneous-layered structure with a blade knife thickness of at least 2.0 mm contains about 25 - 30 carbide layers. Closer to the cutting edge, where the thickness of the blade knife is not more than 1.5 mm the number of layers is reduced to 10 - 15 pieces. The cutting edge is formed in such a way as to form a “micro-saw” of different types of layers of no more than 6 pieces (Figure 5(b)). The hardness cutting edge
Figure 5. Structure of the knife blade of genuine Damascus steel (Ds15P): (a) Longitudinal direction (butt); (b) Transverse direction (cutting edge).
blade knife was not less than 54 HRC. Thus, the hardness near the cutting edge on 12% is greater than the hardness near the butt.
The frontal direction was of the investigated chemical composition of the dark (troostite) and light (carbide) layers that are clearly observed in the structure of genuine Damascus steel (Figure 6). The method of microprobe chemical analysis revealed segregation areas in which the constant impurities of silicon, phosphorus and sulfur are concentrated. The dark layers of troostite (Spectrum 1 in Figure 6) constitute high purity steel containing 99.11% Fe, 0.86% C and 0.03% Si. Other impurities were not detected. At the interface of the troostite-carbide layers (Spectrum 2 in Figure 6) the impurity concentration of silicon and phosphorus increases from dark troostite layer to light carbide layer. Light carbide layers on chemical composition represent pre-eutectic white cast iron (Spectrum 3 in Figure 6). In particular, sulfur impurities of 0.14% S and phosphorus 0.38% P are concentrated in the carbide layers, which significantly affect the carbon liquation during the crystallization of the ingot.
For a more profound understanding of the phase structure, it was decided to carry out x-ray phase analysis of samples from genuine Damascus steel type Ds15P. In Figure 7 shows the XRD pattern indicating ferrite (iron α-Fe) and cementite (carbide iron Fe3C) phases. The volume ratio between the ferrite and cementite is not possible to determine due to the imposition of all the diffraction lines of ferrite on the diffraction lines of cementite. Intermediate phases such as iron phosphide or residual austenite, which can be formed during the
Figure 6. Analysis of dark and light layers of the genuine Damascus steel (Ds15P).
Figure 7. X-ray diffraction diagram and macrostructure of genuine Damascus steel (Ds15P).
crystallization of ingot, were not detected by x-ray phase analysis. This is probably due to the fact that in the process of thermodynamic treatment, phosphorus, with an average mass fraction of about 0.19%, is able to completely dissolve in ferrite without forming a phosphide eutectic. As a result, as the impurity phosphorus greatly distorts the crystal lattice iron suppressing the formation of austenite during heat treatment.
According electron microscopy (Figure 8(a) and Figure 8(b)) it has been found that the matrix in the genuine Damascus steel Ds15P is a lamellar troostite with an interlamellar spacing of not more than 100 nm. Lamellar troostite is formed because of isothermal quenching, for example, in superheated lead to 400˚C or in molten fat at the temperature 200˚C. Thus, the microstructure of genuine Damascus steel Ds15P is a “troostite hardening”, with an interlamellar spacing of about 0.1 µm, in which there are oblong particles of excess cementite with an axis ratio of 1/3.
Let us consider in more detail the carbide layer of genuine Damascus steel, in which most of the carbides have an oblong shape. The elongated particles of excess cementite with an axis ratio of 1/3 are the main distinguishing feature of genuine Damascus steels from the excess carbide phase of modern carbon Tools steels. The oblong form of excessive cementite was mentioned in the works, in which the genuine Damascus blades were studied with a significant excess of phosphorus admixture from 0.12% to 0.22%  -  . This form of secondary cementite is absent in the works on the plasticity of high-carbon steels such as UHCS, containing from 1.0% to 2.1% carbon   . This form of secondary cementite has not been found in the works on the formation of the structure of high-purity Bulat steel type BU22A  -  .
The dimensions of oblong carbides in the cross section area about 3.4 microns, and in the longitudinal section do not exceed 9 - 12 microns. The chemical composition of the isolated excess oblong carbides showed that they have somewhat inflated carbon values of about 7.06% C (Spectrum 1 in Figure 9), compared with cementite 6.67% C, indicating imperfection of the crystal lattice of these carbide formations.
The steel matrix, in which the oblong excess carbides are located, is heavily contaminated with harmful impurities such as sulfur of about 0.14% S and
Figure 8. The microstructure of the genuine Damascus steel (Ds15P): (a) Scanning electron microscopy; (b) Transmission electron microscopy.
Figure 9. Composition of the main structural phases of genuine Damascus steel: Spectrum 1―Oblong carbide cementite; Spectrum 2―Troostite matrix.
phosphorus of about 0.38% P (Spectrum 2 in Figure 9). The excessive amount of phosphorus and sulfur impurities in the steel matrix not only affects the carbon segregation during the primary crystallization of the ingot, but also influences the formation of carbides of an oblong shape during secondary crystallization during plastic deformation by forging.
In the areas adjacent to the elongated carbides, phases of residual austenite are observed. However, their volume ratio is so small that this phase can be neglected in further consideration of the structure of genuine Damascus steel (Figure 10).
Detailed consideration of oblong carbides revealed that these formations are not monolithic. The carbides microstructure consists of individual particles cementite in the form of “pebbles” (Figure 10(a) and Figure 10(b)). Individual cementite particles are tightly coupled to each other. Large oblong carbides in the deformation process can be divided into separate parts, according to the zones of conjugation of oblong cementite particles (Figure 10(a) and Figure 10(b)). They are radically different in morphology from Widmannstatten cementite, globular cementite, carbides cementite network and faceted excess carbides. From our point of view, oblong carbides cementite it should be considered a separate form of cementite inherent in genuine Damascus steels.
There are several different opinions about the nature of the formation of carbide layers in genuine Damascus steels, containing from 1.1% to 2.1% carbon. Some of them are reduced to the fact that the carbide layers are formed because of low-temperature forging in the range 650˚C to 850˚C. In this temperature range, excess secondary cementite does not dissolve in austenite. In the process of low-temperature forging occurs crushing it into separate parts. Only in this range of forging temperatures, patterns are preserved in Damascus steel. Thus,
Figure 10. The microstructure of the oblong cementite particles: (a) transmission electron microscope; (b) schematic of oblong carbide.
according to the authors      , the excess carbides in the genuine Damascus steel is a globular shards of fragmented cementite network. The formations of such structures are described by the mechanism of Wadsworth-Sherby  .
Another opinion on the nature of the formation of carbide layers is that large oblong carbides formed during the crystallization of the wootz ingot. It is assumed that in the process of crystallization of the ingot in interdendritic zone occurs a segregation of the impurities phosphorus. At isothermal exposure, these areas are saturated with carbon up to the eutectic state    . In their opinion, with further cooling of the ingot in these interdendritic zones, are formed primary carbides of cementite not in the form of ledeburite, but in the form of massive isolated particles cementite. The formation of excess primary carbides in the form of massive particles cementite during the crystallization of wootz ingot is explained by the mechanism of Verhoeven-Pendray   .
It was decided to confirm or refute these hypotheses during the reconstruction of the original structure of genuine Damascus steel. For this wootz ingots were prepared by crucible melting with the addition of phosphorus-containing additives. The admixture of phosphorus, having a high coefficient of liquation, contributed to the process of carbon segregation in the interaxial intervals of dendrites. In the process of cooling of the ingot in the interdendritic zone were formed oblong carbides (Figure 11(a)). Probably, the morphology of carbide formations depends not only on the parameters of forging and heat treatment, but also from chemical processes occurring on the border of oblong carbides and pearlite matrix. In this zones there is of phosphide eutectic (Figure 11(b)).
For a more complete flow process, segregation of impurities, a wootz ingot was annealed long in a furnace for at least 5 hours at a temperature of 1150˚C. To prevent decarburization cast samples were annealed in ceramic crucibles. At such isothermal exposure, the solidus line, in the iron-carbon state diagram, shifts to the left up to the eutectoid point corresponding to about 0.8% of carbon. Axial areas of austenite dendrites were released from impurities to hundredths and thousandths of percent, which leads to an increase in deformation
Figure 11. The microstructure of the cast wootz ingot: (a) Primary carbide heterogeneity of the wootz ingot (light areas); (b) The oblong carbide with zones there is phosphide eutectic.
plasticity under normal forging conditions. The interdendritic zone is saturated with excess carbon and impurities phosphorus, silicon and sulfur. Thus, interdendritic zone represent to the pre-eutectic white cast iron. The crystallization point in the interaxial areas is reduced to a temperature of eutectic decay corresponding to about 1147˚C. Further cooling of the wootz ingot can occur in an accelerated mode.
The subsequent forging of the annealed wootz ingot occurred at a temperature above ACM at 30˚C - 50˚C. The proof of this statement is the complete absence in the structure of the fragments of cementite, arising from the crushing of the excess carbide phase in the process of low-temperature forging. Low speed of diffusion of phosphorus in austenite matrix contributes to the slow decay of the resulting segregation of carbon in interdendritic intervals, which can significantly increase the temperature of heating for forging, without loss of carbide heterogeneity.
As a result, the microstructure of the carbide layer in genuine Damascus steel consists of oblong cementite particles located in the pearlite (troostite) matrix (Figure 12(a)). This conclusion is confirmed by the photography of the fracture of the carbide layer is made on the scanning electron microscope (Figure 12(b)). Thus, from our point of view, the oblong form of cementite is a distinctive feature of high-carbon steels with high phosphorus content. Tenths of a percent of phosphorus impurities not only contribute to the segregation of carbon in the interaxial areas of dendrites, but also forms a cementite in the form of massive oblong carbides.
We believe that the formation of oblong carbides in genuine Damascus steel occurs by the mechanism of Verhoeven-Pendray   . That is, when large oblong carbides were formed during the crystallization of the wootz ingot. Long-term high-temperature annealing increased structural heterogeneity. Forging the blade took place in the temperature range from 940˚C to 740˚C. In this temperature range, the carbide heterogeneity acquired a layered texture. It is noticed that some part of small cementite particles dissolving in austenite. At the same time, they again released in the process of deformation in the form of oblong carbides of smaller size.
By the mechanism of Wadsworth-Sherby  is the place to be in carbon
Figure 12. The microstructure of the forged wootz ingot: (a) Carbide layer after forging (optical microscopy); (b) Fracture of carbide layer (scanning microscopy).
Tool steels type У15A. In such steels, the excess cementite is completely dissolved in austenite at the temperature of heating for forging equal to about 940˚C. Secondary allocation of the excess cementite from the deformed austenite is in the form of spheroids evenly is distributed along the entire of the blade knife. For modern cutting tools, this structure is ideal. However, it does not correspond to the macrostructure of genuine Damascus steel. Therefore, to obtain patterned blades knife from steel У15A must be forged in the temperature range just above 723˚C, that is, in the range 850˚C - 650˚C. As a rule, the patterns in such blades knife are small, and the matrix has a grayish tint.
Analyzing the above, we believe that the increased content of phosphorus in genuine Damascus steel explains the mechanism of formation of the macrostructure visible on the frontal surface of the blade knife in the form of a pattern “Kara-Taban” (Figure 13(b)). The pattern is formed in the process of forging an inhomogeneous dendritic structure of the ingot. The development of carbide heterogeneity is favored by the segregation of phosphorus impurities in the interaxle areas of dendrites. Elongated dendritic axes and interaxial zonas, because of the forging of the wootz, form a set of parallel layers (fibers) in the longitudinal and transverse section consisting of oblong cementite carbides.
In the process of forging ingot on the frontal surface of a steel strip are formed of the convexity and concavity, resembling topographic contour (Figure 13(a)). Near the local maximum (convexity) and the local minimum (concavity), the contour of the carbide inhomogeneity acquires elliptical of the lines pattern. Near the geometric saddle, the contour of the carbide inhomogeneity is a set of hyperbolic lines pattern. After polishing and etching in a 4% solution of nitric acid on the surface of the blade knife a light contour of carbide heterogeneity appears on a dark background of the troostite matrix, resembling a pattern “Kara-Taban” (black-shiny).
According to collectors of edged weapons, many genuine Damascus steel, along with a beautiful large pattern such as “Kara-Taban”, have high hardness, reliability and cutting ability. Despite all the achievements of metallurgy in recent years, there is a strong opinion that the blades of modern carbon Tool steel have lower properties than the blades of genuine Damascus steel. The question arises whether the blades made of genuine Damascus steel have always been so good in operation, or is it just a beautiful legend?
Figure 13. Scheme of the blade knife (a) and patterns genuine Damascus steel (b).
Back in the XI century, the Khorezm scientist Al-Biruni (1038)  drew attention to the fact that the blades of the Indo-Persian steel break when struck in the cold. Professor Gaev (1956) confirmed the low level of cold brittleness in work  , who studied the saber blade of the XVIII century from the collection of the State Hermitage museum. Combat Damascus blade containing 1.97% carbon and 0.136% phosphorus from the impact was broken at the hilt and welded with iron. Today we know that a characteristic feature of high-carbon phosphorous steels is the reduction of impact strength at low temperatures (cold brittleness).
One of the first conducted bending tests genuine Damascus steels was the Austrian Metallurgist Zschokke (1924)  . The studied samples of genuine Damascus steel of content 1.342% - 1.874% carbon with increased content of 0.086% - 0.172% phosphorus; not all other elements exceeded hundredths of a percent. The results of static tests led him to a paradoxical conclusion. Static bending properties of ancient Damascus swords were inferior to the industrial bladed steel, made in Solingen. In his opinion, a huge impact on the reduction of the mechanical properties of genuine Damascus steels affected phosphorus, which is present in a significant amount in all the samples.
Checked in detail out the main findings of Zschokke of the American researchers Verhoeven and Jonas (1987)  . They studied in detail the influence of various impurities on the formation of patterns in genuine Damascus steel. Clearly show the possibility of formation of carbide strips during forging. Form the main features inherent in the Damascus steel. As a result, a team of authors from the United States managed to develop a method of reproduction of Modern Damascus blades without harmful phosphorus impurities.
Great job, for understanding the structure and properties genuine Damascus steels, held Dr. Taganov and PhD. Kalinin (2009)   , examining dozens of Indo-Persian blades, collected by expeditions of the Russian Geographical Society. In their opinion, the abnormally high content of phosphorus in genuine Damascus steel explains the mechanism of formation of a pattern such as “Kara-Taban” (black-shiny). The values of the mechanical characteristics of genuine Damascus blades reach no more than 75% of the properties of modern carbon Tool steels, which have no more than 0.01% phosphorus impurities in their composition.
Unlike our predecessors, we did not set ourselves the task to find out the complex of mechanical properties in static tests. Realizing that each blade knife has its own design features, we decided to limit ourselves to determining the hardness, determining the resistance of the cutting edge, determining the growth rate of the fatigue crack as a category of reliability under variable loads. The data were compared between layered samples of genuine Damascus steel type Ds15P (Figure 14(a)) and homogeneous samples of carbon Tool steel type У15A (Figure 14(b)).
An interesting feature of the sample made of genuine Damascus steel is the heterogeneity of hardness indicators both on the butt and on the edge of the blade. On the butt of the blade, hardness does not exceed 48 HRC. On the cutting edge of the blade could reach 54 HRC. The hardness of the homogeneous sample of carbon Tool steel type У15A was not less than 52 HRC. We can say that the average hardness of the samples of genuine Damascus steel and modern carbon Tool steel are the same. With this hardness, the samples have good elasticity with satisfactory resistance of the cutting edge. However, when the diameter of the diamond indenter imprint is about 2.5 mm when measuring Rockwell hardness and the size of the structural components in Damascus steel does not exceed 100 µm, then it is impossible to correctly determine the contribution of a structural factor to the integral hardness of the blade. We believe that this problem can be solved by measuring the microhardness.
Samples of modern carbon Tool steel (У15А) have a homogeneous structure, that is, of the excess globular carbides are uniformly arranged in the troostite matrix (Figure 14(b)). The microhardness values are in the range of at least 400 - 600 HV (50 - 52 HRC) (Figure 15).
The structure in genuine Damascus steel (Ds15P) is most reminiscent of the Natural Composite Materials (NCM) created in the process of forging blades (Figure 14(a)). The microhardness distribution is the minima in the troostite layers from 390 HV to 560 HV and the maxima in the carbide layers from 820 HV to 1020 HV (Figure 15). The distribution of microhardness in the samples of genuine Damascus steel confirms the self-sharpening effect of the blade edge, the so-called “micro-saw” (Figure 5(b)). The essence of the self-sharpening effect is a faster wear of the troostite layers compared to harder carbide layers.
Figure 14. The microstructure of the steels: (a) genuine Damascus steel; (b) carbon Tool steel.
Figure 15. The microhardnessof the high-carbon steels: (a) Damascus steel (layered structure); (b) Carbon Tool steel (homogeneous structure).
A large divergence of the data on microhardness in the troostite layer from 390 HV to 560 HV is associated with uneven distribution of dissolved phosphorus. As the impurity introduction, phosphorous distorts the crystal lattice of the solid solution, which contributes to hardening of the ferritic in troostite colonies. The lowest hardness is observed in the middle of the troostite layer (390 HV), where the phosphorus impurity is minimal 0.02% P. In the transition zone, at the edge of the troostite layer microhardness increases to critical values (560 HV), which is associated with an increase in phosphorus impurity to 0.2% P.
In carbide layers, due to the heterogeneity of the distribution of elongated carbides in the troostite matrix, the hardness depends not only on the increased phosphorus content of 0.4% P, but also on the effect of punching and damping of the diamond indenter. It is impossible to say which structural phase will be under the imprint of the diamond indenter (the “Iceberg” effect). Oblong cementite particle is able of pushed in the softer troostite the matrix, showing lower values of microhardness 820 HV. Conversely, in troostite the matrix of the carbide layer, the imprint of the diamond indenter can dampen, if under layer is hidden a particle of oblong carbide, which leads to an overestimation of the data on hardness 1020 HV. As a result, the average hardness in carbide layers is 920 HV, which is consistent with the data of Dr. Gaeva (770 - 1000 HV)  and Dr. Taganova (average 800 HV)  .
Individual methods for testing the durability of the cutting edge are very much. However, there are no uniform rules for testing. Therefore, the test samples can be compared only with each other. To obtain reliable test results, the human factor was excluded. A load from 2 kg to 12 kg regulated the cutting force. Nature of the cutting was determined by the reciprocating mechanism as shown in Figure 3(a).
With a small force on the cutting edge equal to 2 kg, genuine Damascus steel is showed of more than 2.5 times of the number of cutting, than modern carbon Tool steels (Figure 16(a) and Figure 16(b)). With minimal force on the cutting edge is the effect of “micro-saw” is likely. With 4 kg of force on the cutting edge 1.5 times (Figure 16(a) and Figure 16(b)) reduces the difference between of number of cutting of steel У15А and of number of cutting of steel Ds15P. With 5 kg of force on the cutting edge, of the number of cutting becomes the same. A further increase in the force on the cutting edge leads to the opposite result. From 6 kg to 12 kg of force on the cutting edge, carbon Tool steel is showed a more number of cutting on the 25% than in genuine Damascus steel (Figure 16(a) and Figure 16(b)). This fact is explained by the fact that with an increase in the force on the cutting edge on the test sample of genuine Damascus steel the main superiority of the layered structure, namely the “micro-saw” of the cutting edge, is lost.
In the ancient swords of genuine Damascus steel, the probability of the presence of hidden cracks increases dramatically. During operation, the microcrack is able to grow to the main crack, preparing the conditions for brittle fracture. Reducing the growth rate of microcracks can significantly increase the service life and reliability of the blade knife during operation. In this regard, of particular importance is the study of the “survivability” of blades knife with a homogeneous structure and with a layered structure.
In genuine Damascus steel type Ds15P with layered structure (Figure 17(a) and Figure 17(b)) fatigue microfracture originates in 2 times faster compared to homogeneous samples of modern carbon Tool steel type У15A. The origin of the fatigue crack depends on the defects of the structure, in particular, on the weakened interlayer boundaries.
Further tests showed that in a sample with a homogeneous structure (У15A) the crack grows to a critical value in fewer cycles than genuine Damascus steel Ds15P (Figure 17(a) and Figure 17(b)). There are no significant obstacles on the way of crack growth in homogeneous structure. This means that in samples
Figure 16. The resistance of the cutting edgein the high-carbon steels: (a) Damascus steel (layered structure); (b) Carbon Tool steel (homogeneous structure).
Figure 17. The fatigue of the cracking resistance in the high-carbon steels: (a) Damascus steel (layered structure); (b) Carbon Tool steel (homogeneous structure).
with a homogeneous structure is controlled of cracking resistance will occur at a lower critical length crack. Thus, for fracture of samples with a homogeneous structure is needed 2.7 × 107 cycles. For fracture of samples with a layered structure is necessary 6.2 × 107 cycles. We can say that in the blade knife of genuine Damascus steel (Ds15P), in terms of fatigue reliability (“survivability”), almost 2 times more service life than in the blade knife of modern carbon tool steel (У15A).
The results can be explained by the favorable effect of the layered structure. In this structure, there are necessarily more weak areas in the interlayer boundaries. Growth of main crack leads to local delamination along the interlayer boundaries. The growth energy of the main of the crack is extinguished to zero. As a result, the mechanism of local lamination along the interlayer boundaries is realized enforce the crack to move in each individual layer. Previously, we have proved that the resistance to crack development increases sharply in multilayer steels, in which a layered structure is formed  . Thus, loss in cutting ability of a genuine Damascus steel compensates is increased the reliability (“survivability”) of the blade knife with repeated fatigue loads.
The methods of spectral, x-ray phase and microprobe analysis show that genuine Damascus steel is a high-purity unalloyed high-carbon steel with a high phosphorus content. It is revealed that phosphorus in an amount of from 0.1% to 0.2%, having a high liquation coefficient, contributes to the process of segregation of carbon in interdendritic zone in the process of crystallization. Interdendritic zone formed carbon clusters, in the process of forging transform into oblong carbides cementite.
Oblong excess carbides on a morphological feature resemble a “pebble” with a thickening in the middle part. The sizes of the carbides in the cross section are about 3 - 4 µm in the longitudinal cross section which does not exceed 9 - 12 µm; axis relation is 1/3. The hardness of carbide layers is about 920 HV. The hardness of the troostite matrix was amounted about 475 HV.
Oblong carbide cementite is radically different in morphology from Widmannstatten cementite, globular cementite, carbides cementite network and faceted excess carbides. From our point of view, oblong carbides cementite should be considered a separate form of cementite inherent in genuine Damascus steels. We believe that the formation of oblong carbides in genuine Damascus steel occurs by the mechanism of Verhoeven-Pendray. That is, when large oblong carbides cementite was formed during the crystallization of the wootz ingot.
Cutting edge of the blade knife of genuine Damascus steel is nothing more than a “micro-saw” consisting of parallel carbide and troostite layers. At the little effort cut (to 4 kg) ancient Damascus steel (Ds15P) shows a greater number of cuts than the modern instrument steel У15А. With an increase, force on the cutting edge from 6 kg to 12 kg carbon Tool steel showed a more number of cutting on the 25% than in genuine Damascus steel. This fact is explained by the fact that with an increase in the force on the cutting edge the main superiority of the layered structure, namely the “micro-saw” of the cutting edge, is lost.
In the layered structure of genuine Damascus steel Ds15P, the fatigue crack propagation from the time of its occurrence until complete destruction occurs at a greater number of cycles than in the homogeneous structure of steel У15А. The blade knife of genuine Damascus steel, in terms of fatigue reliability (survivability), has almost 2 times longer service life than the blade knife of the modern carbon tool steel type У15А. Thus, loss in cutting ability of a genuine Damascus steel compensates increased the reliability (“survivability”) of the blade knife with repeated fatigue loads.
For assistance in conducting joint research works, the authors express his deep gratitude to the staff of the Department “Materials Science in Engineering” of Novosibirsk State Technical University.