TWI336730B - Method of metal performance improvement and protection against degradation and suppression thereof by ultrasonic impact - Google Patents

Description

336730, IX. Description of the Invention: [Technical Field] The present invention relates to a method and algorithm for improving metal properties and protecting metals by ultrasonic shock against metal degradation and suppression. The present invention can solve the problem of deteriorating metal characteristics during extended work under the influence of external forces, thermal fluctuations, and unfavorable environmental factors. The present invention protects (i.e., prevents) and inhibits the risk of material damage due to undue changes in performance over time. This type of problem can occur, generally due to the influence of the known conditions of the ship during the environmental degradation of the metal, causing damage to the original structure of the material/metal. [Prior Art] It is known in the art. U.S. Patent Nos. 6,171,415, 6, 289, 736, 6, 458, 225, 6, 338, 765, 6, 722, 175 and 6, 843, 957, and U.S. Patent Application Serial No. 1/834,180 And other technologies, there are many methods and devices, which are related to the direct influence of ultrasonic shock treatment on the material and characteristics of the material strip. This means that the surface of the material and its subsurface layer are the influence and result. main content. Deformation is known to have many forms (classifications), causes, physics, and mechanisms. For example, in Berman AF's "Degradation of Mechanical Systems" (Novosibirsk: Nauka, 1998, p. 32), this document reveals the structural and structural studies and structural results of the material-free degradation process within the structure. The breakdown of the unique mechanical system affected by the rupture' and the combination of many factors. Among them, the process of material damage and structural component 5 damage caused by cracking of rot, gas embrittlement, corrosion, and mechanical fatigue and erosion are also mentioned. The results of experimental research, testing and work experience of mechanical systems (MS) are the basis of information to deal with issues related to the reliability and safety of supporting, maintaining and restoring Ms and technical systems (TS) containing mechanical systems. . This file also handles changes in Ms reliability due to degradation. Degradation of μ means irreversible changes, malfunctions, and dangerous operations in technical conditions. The degradation of the MS is part of the process of damage and accident accumulation, which changes the load carrying capacity of the structure and structure. In order to provide reliability during the manufacturing phase, efforts must be made to study and improve design charts and models based on an understanding of possible degradation processes, establish diagnostic features, damage criteria and limiting states, and validate test methods to determine diagnostics and predictions. Technical conditions, as well as protection against accidents and accidents. To ensure reliable and safe operation, understanding the degradation process ensures effective control and evaluation of the technical conditions of the MS and the causes of its changes, thereby updating the life and diagnostic frequency of the part, thereby enhancing diagnostic and predictive techniques and updating the MS. Mechanical systems form the structural basis of almost all technical systems. Therefore, the strength and life of the structure and mechanism under load are the most important in general methods such as research and maintenance of reliability. The damage of the MS and the exhaustion of the life of the part are characterized by damage and limited release standards. "Operational safety and required life, by retaining the working capacity and load bearing capacity, and compensating for the dispersion of external effects and Obtained by diagnostic and predictive techniques for stochastic properties. '1336730 纟In the past few decades, the causes of damage in the power engineering, chemical, petrochemical, and transportation industries have been studied in detail. The complexity and diversity of this phenomenon has been demonstrated, and its causal relationship is the main cause of depletion (degradation) and destruction of milk life. For example, the damage in the chemical reactor showed a crack in the heat exchange tube that penetrated the tube wall due to an improper combination of thieves, physical and chemical effects. This situation is very likely to occur because of design incompleteness and designation, manufacturing and inspection techniques and operations, incomplete conditions, etc., and violations of the above regulations. As a result, issues such as the strength and longevity of MS and its components are completely unresolved, especially with unique external factors and small MS and TS, which can lead to significant economic and social consequences.曰 - 胄 One way to solve this problem is to combine material and structural mechanical mechanics with stochastic process theory. This method is the basis used by the MS reliability theory. The likelihood of degraded damage should be quite small and within the limits of life expectancy and can be obtained by proper maintenance systems and life design considerations that detract from the physical characteristics of the damage. Here, only based on the mechanical, physical and chemical properties of the damage (4) (that is, the availability of the design model for the damage characteristics), the mechanism and dynamics model of the degradation process, and the quality space of the entire MS and its individual parts. (with operable conditions), can produce an effective calculation of the life. However, the unique operating experience of chemical treatment systems has shown that due to the simultaneous effects of mechanical, physical and chemical factors, it does produce damages that do not produce reliable life predictions, but they do not A design that evaluates the technical conditions and repairability of the MS. 7 In this case, a large degree of damage is caused, because under experimental conditions (the combination of high pressure and temperature, active and aggressive environments, including fast moving objects, many degradation processes that cannot be accelerated) Rate), due to the non-reproducibility of external factors, can not produce appropriate experimental research results. Undoubtedly, inadequate experimental research and testing, as well as the lack of proper standards and limits for damage, can result in improper maintenance. The parametric reliability theory is based on many computational reliability parameters, including many physical and mechanical failure modes. This theory implies that the output parameters of the product change due to the wear and tear of individual parts. However, in many cases, the output parameters are affected by a corrupted value when the function terminates or some critical conditions such as safe operating conditions are met. For example, rupture can occur in containers, tubes, and other parts, and function stops due to cracking or chipping through the inner wall. In this case, some parameters are explicitly pointed out as a characteristic of the danger of penetrating crack formation or hydrogen embrittlement (crack depth or length, etc.). With the existing controllability and diagnostic equipment of many MSs, these parameters are often uncontrollable or inadequately controlled. Therefore, the reliability of such MS should be maintained by analyzing and evaluating possible and hypothetical damage. The results obtained can be used to prevent the expansion of damage and provide safety. The damage of the MS is in the final stage after the destruction of one or several parts, which is picked up by the damaged material that reaches the critical value. Different parameters can be used depending on the material = external factor and as a measure of damage. Damage parameters are characterized by changes in the physical, chemical, and mechanical properties of the material, as well as surface and structural conditions. ^1336730 Basically, existing measurement techniques are not aware of the initial damage phase, either because of their local application or because the industry lacks the necessary technical means, so this must be considered during MS development. As such, a problem arises by identifying the characteristics of direct and indirect diagnostics and developing the diagnostic methods needed to assess and predict the state during testing and work. Describe the relationship between the characteristics of a material and the state of the state under the combination of different factors, which is roughly non-linear. These processes are primarily based on empirical research and formalization. Moreover, under different combinations of external factors, there is a problem associated with assessing and predicting the dynamics of material damage. Many of the roles in MS and TS, especially in chemistry, petrochemistry, nuclear engineering, bioengineering, and pipeline public construction, can cause many different degradation processes, which become complex damage to materials, exhaustion of life, and damage to MS. Wang Yin. Identifying possible degradation processes is the most important goal in pre-design research and design. A number of metallographic physics, metallurgy, physical chemistry, strength, longevity and other research and testing have been carried out to study these processes. The purpose of this type of research is to identify the mechanisms, mechanics, and kinetics of changes in structure and properties based on initial parameters. G p_ — The edited topic 'and' is the latest and most comprehensive achievement of combining the different methods to study the damage process occurring in materials and structures. In "no more than h shape" such as structurai Rdundancy ^ A widely used and reliable method that cannot be applied; S on which the broadcast method provides reliability or positive 9 beats according to the strength and life criteria 336730 The actual assessment. For example, the main failure criteria for pipelines, tubular devices, pressure vessels, etc., are seal damage caused by damage to the pipe wall or damage to parts that would cause leakage or atmospheric injection.

Any damage process can be described by its mechanism, mechanics and dynamics. The mechanism of the damage process means that the factors that determine this process are ''and the interaction between 〇 and ;; mechanics means that the two events, such as microscopic and/or macroscopic events, occur because of the total or accumulation of many basic movements. And dynamics means that the speed of this process changes over time. Therefore, the damage mechanism (degradation mechanism) is confirmed by many factors that affect the composition of the material. The mechanics and kinetics are the timely response to a specific action by the material in the microscopic volume and the submicro volume (SUbmicrovolurae). Confirmed; and, the damage parameters are confirmed by a series of external actions within the part volume. Each damage process is a collective process that is accompanied by a combination of many actions with specific causal relationships. Any deduction process has a minimum number of major dominating factors that are generally adopted as the basis for classifying this process. It is confirmed that the nature and cause of MS material destruction are quite basic, and are described as follows: design model basis for evaluating strength and life; criteria for correct selection of test methods and conditions; verification of initial diagnosis for Ms News. In terms of the persistence and reliability of MS, the μ mechanism, "A and parameters should not only be studied as a consideration of manufacturing technology and rational choice of composition or structural material d but also mainly for setting damage and limit states, periodicity and control Diagnostic methods, prediction methods used in technical conditions, and criteria for reliability 10 蚵 336730 and safety. Metallographic physicists and metallurgists use the term “material destruction”, while strength and reliability experts use the term “composition material damage” or “component damage”. Under the influence of stress, the chemical activity of the material will increase, and the degree of increase will be greater under the influence of periodic stress. Therefore, the study of strength and longevity should not be limited to mechanical standards. Corrosive mechanical damage that causes damage to Ms parts is the main cause of damage to equipment such as chemical, petrochemical, petroleum processing, power facilities, and gas and oil pipelines. This equipment is designed for use in thermal mass conversion processes and primarily for the transportation of chemicals such as petrochemicals and power technology. Material damage is described as a multi-stage 'statistical and large-scale process because it has different damage micro-mechanisms, statistical relationships of thermal fluctuations over time, and in nucleus, dislocation (disi〇cati〇n), Simultaneous phenomena of substructure and structure. Using only mechanical criteria to assess the strength and longevity of a combination of load and medium does not guarantee accuracy and does not allow for the improvement of these criteria or the damage process. According to the results of experimental research, testing and control work, it can deal with some of the most common physical and mechanical properties of the material damage process, which are still poorly understood, such as corrosion cracking (cc), hydrogen embrittlement (HE), corrosion fatigue ( CF), mechanical fatigue (MF), etc. An important factor is detected as the primary cause of one or the other degradation process, and the damage parameters describing each process are identified. Table 1 shows the classification of some of the main factors that contain different damage mechanisms and can define the damage process and parameters. The damage caused by these major factors can be implemented under different factors, factors, individual components of each factor, and additional factors that trigger and accelerate the process. Table 1 The main parameters, mechanism and process classification of a material-free damage The damage parameter (combination of factors) The contact process of the damage process with the direction of the single crack and the external environment; the tension of the meal or intermittent Static stress; material corrosion rupture susceptible to an external environment and contact with the hydrogen-containing environment; tension gray force; periodic sudden temperature fluctuations; welding squeaking zone '' hydrogen embrittlement single crack and active external environment X interaction; periodic stress; sensitive material corrosion fatigue - low cycle and 咼 periodic stress mechanical fatigue surface local corrosion damage (holes, depressions) 0 solution and interaction of static slit zone contact; electrolytic potential Electrochemical heterogeneity of alloys; Irregular stress deformation state 8. Electrochemical corrosion of materials with general uniform or uneven decomposition and electrolyte contact interaction; Environment b pH value; Surface passivation characteristics: Thermodynamically unstable material te" f scraping: the sublimation or decomposition of the material is connected with the temperature or non-electrolyte Interaction; environmental pressure chemical corrosion surface fluctuation changes i multi-moving gas, liquid, abrasive material alone or in combination; environmental speed and temperature; abrasive material amount and hardness; material wear and heat resistance invading micro-cracks, Porosity at grain and substructure boundaries is exposed to high temperature and tensile stress latent changes in mechanical and physical properties. Surface layer is added; residual stress 4 forms high temperature and high pressure in hydrogen-containing environment; sensitive material hydrogen Corrosion - high temperature and high pressure in nitrogen-containing environment; presence of nitride-forming elements in ferritic low-alloy steel: strengthening of residual heat fluctuation process of nitrogen rot and diffusion of impurity elements 'neutron spectrum and neutron radiation intensity; high temperature; ferrite Body steel; impurities (especially copper and phosphorus) Radiation embrittlement 12 "1336730 Table 2 shows the classification results of the most common and dangerous several damage parameters, which have a great influence on the life of the MS and both use cracks as their Characteristics. Table 2—Crack parameters intensified classification Fractures in cracks in front of cracks The type of damage at the tip of the microcrack is semi-circular at the tip of the giant crack; semi-elliptical; straight single focus; multifocal grain inside; intergranular, combined result strong branch; fragile branch; Types of gaps; length formation and joint of holes; types of gaps and localized corrosion fragments; fractures; incisions are known to "accelerated aging of materials and structures: effects of long-term high temperature exposure" (NMAB) The issue of developing test procedures for different materials used in the aircraft industry allows for reliable prediction of the life of new aircraft parts and their degradation during operation. In order to predict the response of material systems to long-term exposure to aircraft structural work environments, A basic understanding of the physical phenomena associated with damage and damage must be made. This is only based on the characterization of experimental materials and the development of relevant mathematical and computational models that describe this physical phenomenon. In many cases, test standards and specifications are available to provide guidance on specific types of part design and test methods. However, for some advanced materials (for example, composite materials), different solutions may be required for material testing, and there may be a lack of standardized methods. Although the requirements for the same basic material properties may be similar, 13 ΓΙ 336730 However, users often develop their own test methods. Different testing methods may result in ambiguity in the test data, leading to uncertainty in material selection, design and manufacturing. Using accelerated testing and analysis methods, it is difficult to evaluate the long-term aging response of materials and structures, especially for the complex conditions encountered in the aircraft service industry. Even though this best technique may not produce a full satisfactory prediction of material performance, however, as new aircraft are designed and materials and structures are evaluated throughout their life cycle, they are developed to provide materials and structures. It is important to have a best understanding of the performance of the test and analysis methods to support material selection and structural design decisions. It is best to have incomplete data in a timely manner to influence critical program decisions rather than waiting for complete and accurate data to be produced. Concerns about the above issues have led NASA to request National Research Council members of the National Research Council to identify problems related to aging of advanced materials' and to propose accelerated assessment programs and analytical methods for the entire working life. During this period, the durability of the future aircraft materials and structures is characterized. Therefore, the NMAB Research Committee developed: (1) an overview of the long-term exposure effects on future high-performance aircraft structures and materials; and (2) recommendations for improved analytical methods and protocols to accelerate experimental testing and analysis techniques to The characteristics and predictions of the material's response to possible aircraft operating environments; and (3) the research required to validate and validate the required testing, analytical capabilities, and evaluation criteria. A general degradation mechanism that must be considered (that is, a physical event or a series of events that form the basis of the observed degradation), including: 14 粦 336730 - microstructure and compositional changes; - time-dependent deformation and synthetic damage Accumulation; an accelerated impact of environmental attack and elevated temperature; and - synergy of the above. From a historical point of view, the main loss mechanism of aluminum alloys in aircraft applications, and the mechanism of decay and fatigue associated with aging fleets. Potential damage mechanisms include microstructural changes, fatigue, creep and environmental impacts. Depending on which characteristics are important in a particular application, the most critical degradation mechanisms are determined. For example, if strength is the most critical, thickening of matrix deposits will be important during periods of elevated temperature; if toughness is the most critical, then grain boundary deposits or areas that produce no deposits will It will be important; and if creep or fatigue is important, the assembly, growth and bonding of microcracks will be important, and the potential damage mechanisms associated with high temperature applications of aluminum alloys include: microstructure changes, fatigue, Potential changes and environmental impacts. Under the influence of applied stress, high temperature exposure can cause many microstructural changes, including: coarsening of matrix precipitates (important in the case where strength is the most critical), as well as grain boundary deposits, or precipitation-free Area (Important in the case where toughness is the most critical) ^Fatigue resistance can be degraded by the accumulation, growth and bonding of voids or micro-cracks. High cycle fatigue resistance is sensitive to micro-crack build-up of microstructure heterogeneity, and the critical value of fatigue crack growth is affected by the degree of residual stress and the crack tip shadowing effect caused by changes in the microstructure. The creep resistance seems to increase with increasing grain size. Moreover, cold working reduces the latent resistance in the reinforced and dispersive reinforced aluminum alloys of the 15 丨 1336730. Degradation mechanisms due to the interaction of the working environment with aluminum alloys include: corrosion, stress corrosion cracking, hydrogen embrittlement, solid metal embrittlement, and liquid metal embrittlement. Three related problems related to the complexity of the fracture process in titanium alloys, as well as the possibility of time/temperature/argon-related damage modes, may hinder the development of niobium strength and 咼 章 刃 , , alloy for use in High-speed civil transport (HSCT) applications. These problems include the effects of microstructure changes in deformation and local rupture' uncertainty in intermittent temperature deformation characteristics, and hydrogen embrittlement. In the long-term high-temperature applications of high-strength and high-toughness titanium alloys for HSCT, the three main factors to consider are: - the effects of microstructure changes that should occur (for example, changes in the size of the caller) , α volume fraction, grain boundary α formation, aging state 'and metastable phase), similar to the effects already produced in aluminum alloys; - the effect of proper operating temperature and loading rate on the properties of the alloy, including: dynamic The possibility of strain aging, the localization of hot start sliding, the effect of time/temperature on hydrogen embrittlement, and the deformation and rupture reaction at the cooling temperature; and—the hydrogen decomposed from an aggressive environment (such as aircraft hydraulic fluid) , resulting in tensile ductility and degradation of fracture toughness. Known by Heloisa Cunha Furtado and Iain Le May et al., "High Temperature Degradation in Power Plants and Refineries" (Mat. Res. Vol. 7, n0. 1 Sao Carlos. Jan./Mar., 2004), this document Reveal the degradation mechanism at high temperatures' and assess the residual life of such damages and operations 16 "1336730 method. The main decay mechanisms in high-temperature power plants are latent damage, microstructure degradation, high temperature fatigue, latent fatigue, embrittlement, carburization, hydrogen damage, graphitization, thermal shock, erosion, liquid metal embrittlement, and different types of High temperature corrosion. In addition, stress corrosion cracking and aqueous solution corrosion can also cause problems, although these damage mechanisms are not necessarily expected to occur in high temperature parts. However, these damage mechanisms can occur when the part is cooled and the liquid is still present in or in contact with it. In the following, each form will be considered. Latent change is one of the most serious high temperature damage mechanisms. The latent changes involve time-dependent changes; .潜 Temperature creep rupture is generally produced in the form of inter-particles in engineering-critical parts that fail after an extended period of time and include: boiler superheaters and other parts operating at high temperatures, petrochemical furnaces Reactor vessel parts, as well as gas turbine blades. At high temperatures, as may occur with local overheating, local deformation may occur, accompanied by large plastic strain and localized wall thinning. At slightly lower temperatures and correspondingly higher levels of stress, the fracture naturally crosses the grains. Microstructural degradation is a mechanism of damage that can be caused by other processes such as latent 'weakness or faster breakage. Microstructural degradation is a mechanism of damage that can cause significant losses in material strength. Fatigue involving repeated stress application can cause damage at high temperatures, as occurs at low temperatures. In high-temperature-operated parts, fatigue is usually generated by a temperature change that causes periodic thermal stress, which causes thermal fatigue cracking. This tendency to rupture occurs in areas with high binding forces' and this detailed mechanism can be one of local latent deformations. 17 1336730 The latent fatigue interaction is a complex process of damage involving creep deformation and periodic stress. Moreover, the main damage mode can be extended from the main fatigue crack growth at higher frequencies and lower temperatures to the main potential. Within the range of damage, where the main latent damage is maintained for a long time and the temperature is the high point of this level. Embrittlement from precipitates can be produced in many different ways. For example, the formation of a sigma phase of a Worthian iron-based stainless steel that is maintained at a high temperature or in a critical temperature range (approximately 565 to 980 Torr) causes ductile loss and embrittlement. When maintained at 550 to 400 ° C The temperature range or the cooling in this range 'fat iron stainless steel may cause embrittlement, if the temperature conditions are controlled to cause such effects, then after prolonged exposure, before the unexpected rupture has occurred, the most It is advisable to carry out a metallographic examination. Except for the embrittlement of the ferrite iron steel exposed to high temperatures during work, and the embrittlement of the Worthfield iron stainless steel by the formation of the σ phase, when the parts are exposed to carbon at high temperatures When the atmosphere continues for a prolonged period of time, the carbonaceous effect will produce a brittle material. Especially the hydrogen damage generated in petrochemical plants can occur in carbon steel by diffusion of hydrogen atoms into the metal, where hydrogen atoms and Fe3c The carbon in the bond combines to form methane and eliminates the pearlite component. This is a special case of microstructural degradation and, compared to the past, is currently less Commonly, this is due to the use of low-alloy steels containing elements that stabilize carbides. After exposure to high temperatures for a prolonged period of time, graphitization occurs in ferrite iron steel because of carburization in the ferrite. The cementite is reversed into 18 ί wide stones, f, phase. It is a special form of microstructural degradation that occurs quite frequently from the chemical composition of the oil. With the development of more stable steel, the above situation is now more Not common, but sometimes it still occurs in petrochemicals and steam generators, because in these cases, the temperature is high and the material is not completely stable. Thermal shock involves rapid temperature changes, which can produce an imminent temperature gradient. And therefore, it generates high stress. Such a load can generate cracks, especially if the shock load is such that the crack generated in this way will be subjected to the thermal fatigue (four) process. Under normal operating conditions, The above h-shape does not occur in thermal power generation waste and refining furnaces, but it may occur during an emergency or during this operating condition. The quality is more susceptible to thermal shock, and ceramic parts, which are more common in advanced gas turbines, are also susceptible to such damage. When particles are present in the flowing gas, erosion can occur under high temperature parts. This is not uncommon in coal-fired power plants. The infested name caused by fly ash will lead to thinning of the wall in the oil and gas reheater. Moreover, the soot blower will lead to the soot blower route. The thinning of the superheater and reheater in the inner tube "For the solution of fly ash erosion, part of it can rely on improving the boiler flue gas distribution and reducing the local excessively high gas velocity. The control side of the soot blower erosion Depending on many factors, these factors include: excessive blowing pressure 'cheek maintenance, and effective pipe protection where needed. Liquid metal embrittlement (LME) can be produced by a combination of most liquid solid metals Λ336730' One of the most serious consequences for the refining industry is the LME of the Worthfield iron-based stainless steel that is zinc. Rapid embrittlement may occur at temperatures above 750 ° C and has been found to exist when there is a source of zinc (eg, galvanized steel structural parts) or when there is contamination from a coating containing zinc, after a fire 'Can produce cracks in the stainless steel parts. The latter source was at the Flixborough disaster (Flixborough, North Lincolnshire, England, 1974), causing considerable cracks. The rate at which cracks are generated (m/s) can be quite fast, and for such cracks, a degree of stress as small as 20 MPa can be produced. Reducing alloy corrosion in high temperature applications can depend on the formation of a protective oxide shell. On the other hand, for alloys having a relatively high strength at high temperatures, it may be necessary to apply a protective coating. The oxides generally used to provide the protective layer are Cr2〇3 and Α12〇3. Corrosion protection creates a failure during the entire mechanical damage of the protective layer, which includes cracking of the oxide due to thermal cycling or from erosion or impact. The above is not a damage mechanism associated with parts that operate normally at high temperatures. However, when the plant is shut down, the fluid may condense and there will be waterborne contaminants in the pipes or containers within the work waste. Corrosion or stress corrosion cracking at low temperatures can cause preferential damage at high temperatures during later operation of the plant. It is known that G. A. Filippov and 〇. V. Livanova (all-Russian conference, structural defects and crystal strength, Chernogolovka 2002) proposed "the interaction of structural defects and the degradation of structural material properties", the document Degradation of tube metal properties after prolonged work is shown by a reduction in resistance to brittle fractures (including brittle 20 1336730 delayed fracture) and is due to strain aging of steel. The document also points out the impact of pipeline extension work on mechanical properties and crack resistance, and suggests the aging mechanism of the pipe. A study was conducted on tube samples from 19 major pipelines that were produced under different climatic conditions. Basic statistical analysis was performed on 17MnSi steels that appeared in more than 80% of all tubes. In order to evaluate the mechanical properties, samples were taken from operating lines, emergency reels and emergency stocks with an effective life of between 4 and 44 years. The metals used in the existing products of the metallurgical work of Orsko-Khalilovsk, as well as the pipes from the emergency stock, were used as initial conditions. Standard mechanical properties such as tensile strength σ Τ 5, undulation strength σ γ $ , elongation δ, and area reduction Ψ do not actually change with the work (refer to Table 3). Within the limits of dispersion, the experimental data is very close to the standard (mouth η at least 520 MPa, δ at least 24%). In order to show characteristics that are susceptible to structural changes, other tests are required, including: samples with increased eviction stress, and samples with pre-cracks; crack aggregation and propagation should also be evaluated. Pipes using sharp notch samples. When tested (refer to Table 3), it was found to reduce the impact strength. After 20 to 25 years of operation, the KCV (impact strength) at 2 〇 γ will drop from 55-70 to 30-50 J/cm 2 . The impact test in the temperature range of _4 〇 and 20 ° C shows that when the life is increased, the critical temperature at which the & metal transforms to brittleness %(T5〇) will move to a higher temperature (see Figure 1). ). After 25 to 35 years of operation, the temperature low temperature brittleness threshold gradually enters a zero upper temperature zone. When the pipe reaches 25 years of work, all the values of the metal breaking strength of the pipe will be reduced, which can be proved by the κ acute gap static test. The plasticity is reduced by about 1.5 = at work. After 25 years, the total fracture energy of the pipe metal will be reduced by almost half, which is mainly due to the reduction of the fracture assembly Αη (see Table 3). The crack propagation will be reduced to a small extent. During the extension of the work, the change in the structural change of the pipe metal has the greatest influence on the crack buildup. Figure 1 shows the brittle state of the pipe metal for the 17MnSi steel (I.)

The effect of the transition temperature (symbol 丨 means at 2 〇. (: the case of the above brittle state transition). Critical crack opening (C0D), reflecting the crack-induced limiting deformation, which is 2G to 25 years after work, dramatic The ground reduction is about 丨·5 times. This means increasing the sensitivity of the steel to stress concentration, that is, it is not very dangerous at first, and the stress concentration on the surface of the pipe (scratches, scratches, dents, etc.) It will become the most important after the work is extended because of the structural change in the metal of the pipe.

Therefore, during long working hours, the tube metal is subjected to structural changes, which results in reduced brittle fracture resistance. This means that the occurrence of the phenomenon is due to the increased resistance of the microplastic deformation and the high local micro stress due to the load. Table 3—Degradation of mechanical properties of 17MnSi-type pipe steel during extended work (7TS MPa ° YS MPa δ % Φ % Αη J/cm2 ΑΡ J/cm2 KCV'40 J/cm2 KCV^ J/cm2 0 594 411 27 59 14.7 28 53 57 20-25 584 419 27 58 Ί 14.4 29 51 55 30-44 572 407 26 56 11.5 23 47 46 22 Ί336730 The toothing of the structural state of the pipe metal can be caused by stress The accumulation process of defects. The rot (four) process will change the surface condition of the tube = genus 'filling the metal with gas, so that micro-cracks = Shao defects can be formed. In the static or quasi-static stress less than the final fracture stress of the steel and (iv) stress, Micro-cracked defects and broken (four) accumulation processes, - generally referred to as "delayed fractures. Delayed fractures are premature brittle fractures of critical high-strength steel details exposed to rot (4), eg, locked bolts, strained Strengthen metal wires, etc.

Delayed fracture testing is performed based on simultaneous exposure to stress, rot, and hydrogen. The delayed fracture has three phases: the incubation period (crack assembly phase), the slow growth of stable cracks, and the external velocity rupture. In the case of possible contact with the environment of the rot, in order to assess the reliable operation of the pipe, the most important assessment is to find the resistance of the crack accumulation and reproduction (not as fast as the impact test, but slower). The degree of impact strength does not reflect the crack formation resistance for the pipe.

Figure 2 shows the relationship between the TF rupture time tf and the initial stress intensity coefficient I. It is for several pipes of the following 17MnS i steel: (丨) just manufactured; (2) working tube; (3) emergency tube. Extending the work will affect the inclination of the tube metal to the delayed fracture, moving the L versus tf curve to the region of lower rupture time. Therefore, if L is the same, the rupture time of the newly manufactured tube will be much larger than that of the working tube and the emergency tube as shown in Fig. 2. The rate of stable crack propagation is also related to life. The metal of the newly manufactured tube has the most unstable rate of crack propagation, about G-3) xl0-4 mm/min. The longer the working life of the pipe, the higher the rate of stable crack propagation, about 32 1336730 is 80xl 〇 _4mm / min 〇 In order to find out why the resistance of the tube metal brittle fracture is reduced under extended working conditions, therefore, Perform a strain aging test. During the extended work, changes in the structural state of the pipe metal can affect the fracture resistance under the most severe conditions (rigid stress riser or low temperature) and, obviously, this is related to the strain aging process. Therefore, it is important to study this process to understand the mechanism of rupture resistance changes.

Strain aging of iron and low carbon steel can only be observed when the solid solution contains a specific concentration of carbon and nitrogen atoms. Strain aging causes increased tensile strength, relief strength, hardness, and plateau on the SN curve; the critical H-degree of increase in impact measurement 4; and the tendency of lower plasticity and strain aging is an important property of metals.

In order to evaluate the above metal characteristics, the sample was subjected to tension (2%) at the relief portion, maintained at 20 (d) for -hour, and subjected to a tensile test. The tendency of strain aging can be obtained by the growth of the fall strength at the end of the active deformation (Δ~= Ισ2,). The higher the degree, the greater the tendency to strain aging. In addition, the area of the pipe (4) in the aging condition is reduced (the plasticity can be estimated. According to Fig. 3', it can be inferred that during the extended working period, the strain of the steel will be lowered, and the old tendency of the steel is also reduced. S and the reduction area in the aging conditions will be smaller. This is the most intensive during the first 15 to 3G years of work. The effect of the work on the deformation aging frequency centripet 5 is shown in Figure 3 and the reduced area of the aging tube Ws is shown in Figure 4. The tendency of no iron to correspond to aging is related to the content of impurities (carbon and nitrogen) in the solid solution in free conditions (ie, combined with the poor row), 24 1336730 It is common knowledge. In order to study the aging mechanism of pipe metal under long working conditions, the internal friction measurement method is used because it is most sensitive to local changes in the structural conditions of steel. The carbon and nitrogen content in solid solution can be It is judged from the result of measuring the internal friction temperature dependence (IFTD). The IFTD curve of a steel containing free carbon and nitrogen is known to have a Snoek maximum near 40 ° C, which is by free crack origin. The movement of the child in the stress field. The more free carbon and nitrogen atoms in the solid solution, the larger the Snoek maximum. After 30 years of operation, the FTD curve of the sample cut from the tube, As shown in Figures 5 and 6, there are two maximums at 60 and 200-220 ° C. After 30 years of extended work, the temperature dependence of the internal friction of the tube metal of 17MnSi steel is shown in In Fig. 5, the dependence in the emergency stock is shown in Fig. 6. In the case of the curve of the sample cut out from the emergency stock tube, the 'S 6GT W maximum value is lower than 胄. When the impurity content of cracks is greater than 2x10-1, it is known that the maximum value of Sn〇ek in the IFTD curve can be observed. Therefore, the following conclusion can be drawn that after 3 years of work, the carbon and nitrogen content in the solid solution of the tube is about 2χ1〇-4%, that is, in the pipeline condition, in the free solid solution Carbon and nitrogen levels tend to decrease. Under pipeline conditions, during the operation of the pipe, due to plasticity (4), the carbon and nitrogen content will be reduced. The difference between the carbon and nitrogen atoms will be affected by the difference between the carbon and nitrogen atoms. The "atmosphere" of atoms and reduces their mobility. Under the pipeline conditions, the correction of deformation aging can be confirmed by the addition of the maximum value of the IFTD curve from _ to 250%, only when the metal is plastically deformed and the aging of _, the above situation is obtained. 25 1336730 Therefore, during operation, the tube is subjected to pressure and temperature differences, as well as dynamic and static loads. Pipe operating conditions can produce possible deformation aging in the metal' resulting in increased differential displacement resistance and increased hazard in the local stress peaks in the metal. Therefore, local stress relaxation in the notch or crack apex is reduced, and the tendency of the steel to be brittle is increased. In order to reduce the brittle fracture hazard of pipelines that have been in operation for more than 20 years, especially after the pipeline is shut down at low temperatures in winter, the enhanced cold and brittleness of the pipe metal caused by deformation aging must be considered during the startup of the pressurization station. Therefore, the following conclusions can be determined: (1) In order to evaluate the conditions of the main pipeline, it is not sufficient to understand the conventional mechanical characteristics. Reliability assessment criteria should include characteristics that are susceptible to local structural changes, such as delayed fracture testing and characteristics obtained from tests performed on cracked or sharply notched samples at low temperatures. (2) After performing a sharp notch bending test on a sample that has been in operation for 25 years, all fracture resistance characteristics of the metal are reduced. The tendency of steel to delay rupture, under the action of stress, corrosive environment and hydrogen, has been found to be particularly affected by structural changes. (3) During the extended work period, the metal properties of the pipe deteriorate due to deformation aging, and the mechanism is the decrease in the concentration of free carbon and nitrogen atoms, and the decrease in the mobility of the difference. Known by UK Chatterjes, SK Bose, SK Roy et al., "Environmental Degradation of Metals (Corrosion Technology)" (Marcel "Hot, 2001"), which reveals that during the processing, storage and operation of metal parts, ' All types of environmental degradation that may be suffered. The coverage includes: basic 26-day forms and prevention of these species 66, P yu /, degradation of one member 9, such as aqueous solution corrosion, loss of precursor and scraping process, alloy oxygen solution Metal intrusion, hydrogen damage, and radiation damage.

It also clarifies the effects of general and local rot, atmospheric exposure, high temperature gases, water, shading chemicals, liquid metal and nuclear radiation: this document also shows how the design of parts changes to reduce the surname; Sulfur and water laurel, element and c〇2 "high temperature and low temperature effect of oxidant; instantaneous and delayed damage of solid metal when contacted with liquid metal; highlights the effect of hydrogen on metal, including loss of ductility Internal flaking, blistering, cracking, etc.; showing the effect of radiation on metals, such as light shot growth, void growth, and embrittlement.

In addition, the above documents cover the following topics: aqueous solution corrosion, loss of f; types and prevention of bismuth and spalling processes (thermal kinetics of metal oxidant systems] mechanical type 15 and rate equations; defect chemistry of oxides and other inorganic compounds Role; mechanism of tarnishing and flaking; scale growth caused by lattice and grain boundary diffusion; formation of voids, pores and other macroscopic defects in oxide scales and substrates; stress and strain in growing scales ; decomposition and diffusion of oxidants in metals; effects of metal surface preparation and pretreatment; alloy oxidation; liquid metal attack, and hydrogen damage. Known by Brigitte Hattat for "accelerated degradation" (amptiac

Rome, NY 2001), this document provides a brief description of the methods of material degradation and accelerated degradation. Product performance is measured as a function of time under conditions of excessive stress by accelerating degradation or aging. It is difficult to characterize the aging or degradation of materials because the actual working environment cannot be simulated in the laboratory at 27 1336730. Periodic or varying loads, temperatures, radiation, humidity, and other effects that affect the environment create interactions that cannot be replicated, especially in the case of flying. However, the new part design is based on materials and structures that have been evaluated throughout the life cycle, resulting in test methodologies and analysis for new designs. According to Nelson's book on accelerated testing (see Nelson, W., 1990, Accelerated Testing: Statistical Models, Test Plans and Data Analysis, W i 1 ey in Probability and Mathematical Statistics) In the book, pages 11 to 49, Table 4 presents the degradation mechanism, the materials it affects, the accelerated stress factors used, and the analysis used to measure the measured characteristics of this reaction. For example, fatigue can occur in materials such as metals and plastics, and the accelerated stress factor can be temperature, load, or chemical reaction. The measured characteristics are the remaining life and the cumulative damage effect. This information helps generate patterns for inference to determine the remaining life. For its part, this is in contrast to an accelerated life test that extends across the entire life of a material or part. Table 4: Definition of Degradation Mechanism, Material and Destruction Degradation Mechanism Material Accelerated Stress Measurement Characteristics Fatigue Metal, Plastic, Glass, Ceramic, Composite Load, Temperature, Chemicals (wage, Hydrogen, Oxygen) Remaining Life, Residual Strength, Cumulative damage to corrosive/oxidized metals, food and pharmaceutical chemicals concentration, activator, temperature, voltage, mechanical load (stress corrosion) based on physical mechanism based on the possibility of degradation model latent metal, plastic temperature and mechanical load, duty cycle Chemical deformation of chemical contaminants (eg water, hydrogen, fluorine) under fixed load 28 Cracking of metal, plastic, glass, ceramics, composite mechanical stress, temperature, chemicals (humidity, hydrogen, age, acid) Deterioration of stability and shelf life Test wear rubber, polymer, metal speed, load (magnitude, type), temperature, lubrication, chemicals (humidity) Degradation of mechanical properties Weathered metal, protective coating (eg: paint , electroplating, anodizing), plastic, rubber Solar radiation (wavelength and intensity), chemicals (humidity, salt, sulfur, ozone) Corrosion, oxidation, tarnish, chemical reaction 1336730 Accelerated aging means accelerated exposure, resulting in end-of-life microstructure or damage for subsequent Characterization test. For example, the coarsening of the microstructure of the metal alloy can accelerate the exposure by reducing the strength and toughness of the material. Both accelerated degradation and accelerated life testing may need to be confirmed when multiple damage mechanisms are involved (eg, thermochemical fatigue). Accelerated aging can be achieved by (1) increasing temperature and load; (2) destroying the article prior to performing the test; (3) increasing the number of holds between exposures; and (4) increasing the chemical that causes degradation The concentration of the agent. Compared to accelerated life testing, accelerated degradation testing has the advantage of analyzing performance before a material or part failure. Degradation testing can determine how much life is still in a material or part, and such knowledge can extend life. Infer performance degradation to estimate when damage is reached and to analyze degraded data. However, such an analysis is correct only when the performance degradation inference mode and appropriate performance impairments have been established. For accelerated aging in situations involving multiple degradation mechanisms, the following steps must be performed in series: the sample must be incrementally exposed to conditions that cause a degradation mechanism until the end of life. 29 1336730 The aging of commercial and military aircraft is important for the US Department of Defense' Space Agency and the Federal Flight Administration. These agencies deal with the monitoring of aging problems such as corrosion and fatigue. Due to its exposure to severe environments, there are special interests in candidate materials used in advanced subsonic aircraft and supersonic applications, including, for example, aluminum alloys, aluminum-based composites, titanium alloys, Body materials such as polymer-based composites. Among the materials used in supersonic engines, φ Wang wants nickel-based superalloys and ceramic-based composites. Due to the intensive use, aluminum alloys have a large information base. The degradation mechanisms of aluminum alloys include: microstructure and compositional changes; time-dependent deformation and synthetic damage accumulation; environmental invasion and temperature rise #acceleration, and the synergy of the above mechanisms. The damage mechanisms associated with the high temperature application of the alloy (e.g., microstructural effects, etc.) are shown in Figure 7. It is necessary to know the expected value of the life of the part from the beginning (time t=G). Depending on the #重·(4), the life can be a few million cycles, or several years. It can be related to the degradation process, such as rot #, fatigue, creep, etc. For example, specific parts such as aircraft parts are made to be applicable to this system, and other parts of the fatigued body have a relatively compact life. The purpose of the accelerated test is to use the stress-operating conditions. The information obtained and tested determine the lifetime of the main failure mode under normal operating conditions. To achieve this, it is necessary to understand the mechanical effects of this failure mode. In the case of accelerated degradation, temperature, load, and duty cycle can be used to determine the life model of the predicted failure mode. This measurable test 4 can be accelerated by increasing the temperature, or by adding 30 1336730 plus load to duty cycle' or by using a combination of all effects. Under stress conditions, this model predicts that damage will occur within a few hours (or minutes). Once confirmed, the same model is used to predict life under normal operating conditions. In the early design phase of a part or device, when hardware details were not selected and material selection was not completed, the concern was to make the system work. The next-to-off (four) focus is on performance optimization, which means how to make the system produce better results first. The next step is to confirm the guidelines for product improvement to meet specifications. On the other hand, the life system is related to the failure mode and is related to the performance maintenance and robustness over the life of the article, as specified in the specification. Damage occurs due to insufficient performance or due to serious or catastrophic failures such as replacement. In this relationship, accelerated testing can be used to determine and extend life, but it can also be used to identify guidelines for performance improvement. Yu Wei, Accelerated Testing is a method for predicting future material and part performance based on currently executed test procedures. This result can be obtained by using a more rigorous test environment than is encountered in a normal environment. Known by Dean·Lee in 1988, “Degradation of Metals in the Atmosphere” (ASTM Special Technical Publication // Stp), edited in accordance with the document of the workshop held in Philadelphia, PA. in May 1986, which reveals Get technical information from recent tests, long-term testing programs, and expertise in the field, including information on new materials in the structure. Known by Gangloff, Rp, Stoner, GE, and Swanson, Re et al. (University of Virginia' Charlottesville Engineering and Applied Science, 31 丨 1336730, died in 1988, “Environmentally Aided Degradation in Aluminum-Lithium Alloys” Mechanism, this document provides an overview of the research requirements for the environmental mechanical degradation mechanism of aluminum-lithium-based advanced aircraft alloys. The progress of the characterization of aqueous solutions and gas environmental corrosion fatigue crack propagation kinetics, microstructure paths, and damage mechanisms for the 2090 alloy was reported for the three tasks. As a result of isolating and measuring the localization process, the summary outlines a one-page study. The above localization process was assumed to be able to control the corrosion and embrittlement of the aluminum alloy. Known as McGeary, F/L., Summerson TJ, and Ai lor, WH et al. (ATSM-STP-435, 1967, 70th Anniversary Conference, "Corrosion of Metals in the Atmosphere", pp. 141-174) Non-ferrous metals and alloys - aluminum bismuth exposure, seven-year data, which revealed the weathering test results of 34 processed aluminum alloys exposed to four ASTM locations in the United States for seven years. Moreover, for comparison purposes, data on three additional aluminum alloys exposed for six years in five locations in the UK were included. Exposure to the industrial atmosphere of Sheffield and London in the UK has been found to produce the greatest degree of corrosion, especially on the sides of the panels exposed at a 30 degree angle to the horizontal. Self-limiting corrosion characteristics can be observed on weathered surfaces at all test sites in both countries. After 20 years, this test will be continued and re-exported as 'as in the previous ASTM B-3 test (ASTM-STP-175) on older aluminum alloys. Known in 1989 by Gangloff, Rp, Stoner, GE and Swanson, RE et al. (University of Virginia, Charlottesville Institute of Engineering and Applied Sciences), "Environmentally Aided Degradation 32 1336730 Mechanism in Advanced Light Metals", Revealing the research program, which aims to produce a quantitative characterization of the alloy properties and to develop a pre-warning mechanism for environmental damage modes. Some projects include: chloride slakes in aqueous solutions of aluminum-lithium alloys (4) Localization mechanism in fatigue; (4) Localized aqueous solution of alloy in the surname <Measure! And mechanism; study of localized rot and stress corrosion cracking behavior of alloy 2_; (10) deformation and cracking of alloy—dissolved hydrogen and low temperature; and high temperature crack growth in high-grade powder metallurgy alloy. Known D.K. Das, Manish R0y, Vakil Singh, and s ν

Joshi et al., "Material Science and Technology", Vol. 10, No. 10, vol. 15th, 1199, 1208, published in the first month of 1999, "Pure white gold aluminide coating on superalloy CM247 during thermal insulation oxidation" Degradation of microstructures, which revealed no experiments, including high-activity pure aluminide coatings and 11 οοχ thermal oxidation of platinum aluminide coatings, resulting from the casting of nickel by package cementat丨〇n technology On the base superalloy CM247, its main purpose is to systematically understand the degradation process of the coating during oxidation. Although the weight gain during oxidation of pure platinum and platinum aluminide coatings is based on parabolic dynamics at the onset of oxidative exposure, the bare alloy appears to exhibit a rather long initial transitional oxidation cycle (approximately 20 hours), exceeding This cycle follows the parabolic rule "the linear constant of the normal line for platinum aluminide coatings, which has been found to be almost less than the square of ten of the usual numerical values used for pure platinum coatings. Although ΝιΑ12〇4' was also found in the case of more than 200 hours of pure aluminide coating, alumina was considered to be the only oxidation formed on pure aluminide and platinum aluminide coatings during most oxidative exposures. Phase. However, the oxide layer on the bare alloy was found to contain Al2〇3, Cr2〇3 and 33 '1336730

NiAl204. The microstructure degradation of pure aluminide and platinum aluminide coatings was found to occur in three different stages during oxidation, however, these stages were different for each coating. This staged degradation is disclosed in detail in this document, which relates to the final elimination of the internal diffusion layer in each case.

Jedlinskia, Jerzy, "Oxidation Initiation Degradation of Coatings on High Temperature Materials" (Proceedings Symp, Temperature Coating, SCI & TECH, 1994, Vol. 1, pp. 75-83), which reveals aggression The interaction between the sexual environment and the material being coated can lead to accelerated degradation of the latter. The understanding of the degradation mechanism plays a very important role in the design of materials with improved working characteristics. Also known in the document is the state of the art in the field of developing coatings in the case of enthalpy applications in oxidizing gases. In addition, the precipitation process of the main types of coatings and the degradation mechanism to improve the oxidation resistance of the coating, as well as the existing problems associated with the protection of Ti-based alloys and C/C composites, are also disclosed.

Know Schtze, Michae Bu editor rib "纣^

The “corruption_environmental degradation” proposed by HaaSen et al. reveals a comprehensive and extensive survey of the whole topic, from basic to the latest research results. As written by the top experts and scholars of the International Group, this document is an indispensable reference for any material science (4), physicist or chemical 所 involved in rot science. Corrosion protection: the most important topic in applied materials science... From an economic point of view, rot is not important, and, due to the characteristics of combined metallurgy, material physics, and electrochemical temples It also has a high degree of interest in science 34 3436730. Today, corrosion science can even gain new impetus from surface science and polymer chemistry. Known by M. Elboujdaini and E. Ghali in 1999, “Environmental degradation of materials and corrosion control in metals”, including documents authorized by experts worldwide, and summarizing aluminum alloys, magnesium alloys and steels Recent developments in the field of corrosion and performance. An in-depth discussion of metal and stress corrosion cracking bans, as well as recent techniques in the application and testing of corrosion monitoring. Detailed topics include: corrosion characteristics of aluminum alloys; prohibition and protection of aluminum and magnesium alloys; prohibition and protection of metals in the treatment industry; auxiliary fracture of steel; stress corrosion cracking; corrosion fatigue; hydrogen damage; Technology; durability of materials; coatings and their properties. R.K. Singh Rama, published in February 1998, Issue 2, Volume 29A, "Role of Microstructural Degradation in the Heat-Affected zone of 2.25Cr-lMo"

Steel Weldments on Subscale Features during Steam Oxidation and Their Role in Weld Failures", which provides the base metal (ie, heat affected zone (HAZ)) near the weld pool caused by the electronic welding of 2.25Cr-lMo steel The characteristics of microstructure degradation and the optical microscopy of different weld areas. In order to study the effect of microstructure degradation on the spalling dynamics of vapor and subsea le, so from the weld Some samples of the base material, HAZ, and weld metal samples were oxidized for 1 hr in 35 pct nitrogen vapor and 873 K. The oxide scales formed in the three regions and the underlying scales can be characterized by using a scanning electron microscope (SEM) with 35 [1336730 and an electron detection microanalyzer (ΕΡΜΑ). The free chromium content in these three weld zones has been studied to protect the formation of scales and the effects on the secondary scales. As a major achievement, this study has clearly shown the formation of oxidative inducing voids in the sub-scale regions during the vapor oxidation of ruthenium and the cavitation of grain boundaries in the surrounding regions. This document also reveals the possible role of oxidatively initiated void formation and grain boundary cavitation in the internal working life of welded 2.25Cr-lMo steel parts. Known by Desi. J. 'Kiss, MS and PE, "The basic types of material corrosion that designers must be able to fully cope with" (DJK Engineering, LLC, published on http://d ikeng.汁彳coniZld3 .html) 'It reveals that all materials that can be formed into useful tools, structures and transportation tools are subject to corrosion. Various forms of corrosion can affect any material. Most of the materials used to support or withstand heavy loads are either metal or steel reinforced concrete. Eight forms of corrosion include: stress corrosion cracking, erosion corrosion, crack corrosion, potential corrosion, intergranular attack corrosion, and joint attack. , dents, and selective leaching. The document also reveals corrosion of stainless steel; corrosion of plastics, composites and ceramics; corrosion control and prevention. It is known that Y. Minami, H. Kimura, and Y. Ihara et al. proposed microstructural changes in Worthite iron stainless steel during long-term aging (Mater Sci. Techn., 2: 795-806, 1986), It reveals the changes in microstructure, the properties of the sink, and the mechanical properties of typical Worthite iron stainless steel (3〇4h, 316h, 321h, 34讣 and tempaloy ai) after prolonged aging. These steels will age statically for up to 50_hours within a temperature range of 6 to 36 1336730. The microstructure change can be observed by optical and transmission electron microscopy, and the residue obtained can be analyzed by X-ray knife. For each steel, make the time / degree of the temple pattern. For samples aged at x, the amount of fine phase was measured. Both hardness and impact values are varied and the tensile properties of the aged samples are measured. It is known that γ·Kojima, T. Takahashi, and M. Kubo et al., in 1981 φ, during the long-term natural aging period, A 1 〇 PCT money alloys are reduced, which are provided at up to about L3 A study of the changes in the mechanical properties of the alloy A1 1 〇pct magnesium alloy during the year of natural aging. The extension of more than 20pct is reduced to only 1 to 2pct in samples with less than three months of natural aging, due to natural aging for more than ten years. By reversing the experiment and the electron microscope, it is possible to show a large drop in ductility due to the formation of a spherical coherent Gp region during the course of natural aging. Transmission electron microscopy (TEM) studies have also shown that the structure of the region appears to be a U(sub 2) structure in which aluminum and magnesium atoms are staggered in a three-dimensional periodicity along the {1〇〇丨 direction. It is known that K. Kimura, T. Kisanuki, and S. Komatsu et al. "cause the degradation of the latent deformation of lCr-lMo-l/4V steel at 550 〇C" (Journal of the Japan Iron and Steel Institute, No. 15) Book 71, pages 1803 to 1810), which is described in 550 due to lCr-lMo-l/4V steel. (: The latent change lasts for 9,500 hours of latent damage, leading to microstructural changes and degradation of latent resistance. Especially 'has been on the latent damage sample (accepted or not reheated), checked The grain boundary voids have a shadow of latent resistance 37 1336730. Metallographic observations have shown three microstructure changes with latent deformation, including: coarsening of carbides that usually occur during tempering, formation of voids and cracks 'and significant recovery near the iron grain boundary of the previous Worthfield. Even in the accelerated creep phase, the degree of carbide thickening is very small, and the effect of the void on the resistance to creep is negligible. The progressive loss 'showing 7F' is closely related to the local recovery near the Worthfield iron grain boundary. It is known from JW Jones and SF Claeys et al. "The role of microstructure instability in long-term creep life prediction. (Pentag〇n Report D026031, 1984), in which aluminum alloy 6061 is used as a model material, while microstructural instability is described for long time The effect of variable life prediction. During the long-term creep, the effect of microstructure change on life, through the use of accelerated aging and short-term creep test, can be determined by measuring the effect of microstructure degradation on the steady state creep rate. At intermediate stresses of 26〇c>c and 288〇c, the creep life is severely affected by the rate of microstructure degradation, and the methods proposed by other workers are also very effective in predicting the creep life. Next, it is possible to properly predict the creep life of nearly 100,000 hours by performing a short-term creep test on a completely over-aged sample, and using sample inference techniques. This result indicates that knowledge of the aging reaction of the alloy can be used. In order to predict the long-term creep life, it has reasonable correctness. It is known that Al. Th. Kermanidis' PV卩 (7) 丫 "(10) "and Lukou 〇

Pantelakis et al., “Corrosion of Aluminum Alloys in Corroded 2〇24 T351 Aircraft&#; Fatigue and Damage Tolerance Characteristics” (Theoretical and Applied Fracture Mechanics, 2 〇〇 5 38, published P, Volume 43, 121-132 Page), which reveals the fatigue and damage tolerance characteristics of the 2024 T351 alloy sample, and the comparison with the characteristics of the material. Experimental studies on the derivation of the pre-corrosion and the fatigue fracture growth curve in the case of exfoliation and the measurement of fracture rupture. The fatigue crack growth test was performed for different stress ratios R. Under the same conditions, all mechanical tests were repeated on uncorrupted samples to obtain reference material properties. For corroded materials, significant reductions in fatigue resistance and damage tolerance can be obtained. The results of this experimental study are discussed in terms of the rot of the 2' chain alloy and the hydrogen embrittlement caused by the rot. It shows the need to consider pre-existing corrosion, the effect on the material properties of the fatigue and damage tolerance analysis of parts with corroded areas. Ming aircraft structures are susceptible to corrosion and fatigue damage, and they primarily interact at structural joints. The interaction between corrosion and fatigue may represent a serious threat to the structural integrity of the aircraft, especially as the aircraft becomes older. At present, the consideration of structural degradation caused by corrosion is related to the existence of corrosion and the load bearing capacity of the corroded structural member and the formation of fatigue cracks. In the corrosion pits, the damage is quantified and is associated with a reduction in the fatigue life of the 2024-T3 sample that is subject to corrosion during the alternate soaking process. The effect of corrosion on damage to multiple locations and the structural integrity of the aircraft is believed to be responsible for the multi-site damage (MSD) that begins at the crater. On the other hand, it was found that the previous peeling of the decay had no significant effect on the rate of fatigue crack growth of the 2024-T351 sample. 39 1336730 The corrosion attack of aluminum alloys is orthodox due to the complex process of oxidation. However, the latest research carried out on a range of aircraft alloys has long proven that corrosion is not limited to known surface damage processes that affect the fall strength and fatigue life through corrosion notches, and that it is also diffusion controlled. The cause of hydrogen embrittlement of materials. For magnesium containing the 6 χχχ series, in addition to the oxidation process, the hydrogen produced during the decay process can diffuse into the material and cause interaction between hydrogen and the metal. Recent research has shown that corrosion can lead to hydrogen embrittlement of aluminum alloys such as 2xxx, 7xxx and 8xxx. Although the mechanism of the embrittlement process has not been fully understood, the identification of different possible hydrogen capture sites is related to the alloy system. This hydrogen embrittlement phenomenon reflects a significant reduction in the ductility of the corroded material region. The macroscopic hydrogen embrittlement obtained can be explained by argon-induced local microplasticity. This process is formulated using the difference row theory. It should be noted that both corrosion and hydrogen embrittlement damage are diffusion control processes, meaning that the mechanical degradation of the material is only partially localized. However, at present, there is no experimental data, or established experimental and theoretical methods, which can be used to evaluate the value of the local material properties of the corroded areas of the material. It should be noted that the experimental study on the interaction between corrosion and fatigue is often related to the fatigue and fatigue crack growth tests performed in a certain rot environment, but the tests performed on the septic material. Irrelevant 'by this, for the actual situation of reading old aircraft, the latter represents a different and more relevant situation. Pre-corrosion 2024 is the combination of the cost and the damage tolerance characteristic, which has been studied and discussed according to the synergistic effect of corrosion and corrosion-induced hydrogen embrittlement. The experiments performed included obtaining a fatigue test of the S_N curve, a fatigue crack growth test, and a fracture toughness test. The fatigue crack growth test was performed for stress ratios R of different values. For the sake of comparison, all experiments were performed for uncorroded materials. The results show the effect of existing corrosion on the fatigue and damage tolerance characteristics of the 2024 alloy, as well as the effect of corrosion on the mechanical properties of the fatigue and damage tolerance analysis of the corrosion region of the structure. A series of measurements of the pore size and the pore size of the aluminum 2024 T351 that was stripped of the decaying for 36 hours have shown an average pore diameter of 2 586 x 10 3 coffee, and a density of 920 samples per 〇〇 mm 2 . The measurement is generated using the normal scene image analysis. Metallographic corrosion characterization shows that some intergranular corrosion can also be expected after 36 hours of exposure to exfoliation corrosion. The presence of major corrosion depressions and intergranular corrosion promotes the onset of fatigue fracture and, therefore, significantly reduces the fatigue life of corroded samples. As expected, the reduction in the fatigue life of the sample subjected to corrosion increases as the fatigue stress decreases. The fatigue tolerance limit is reduced from 175 MPa for uncorroded materials to 95 MPa for pre-corroded samples. Regression analysis can be used to derive suitable curves for uncorroded and corroded materials. In all cases studied, the fatigue crack growth resistance of the corroded sample appeared to degrade faster than the fatigue crack growth resistance of the uncorroded sample with increasing fracture length. This results in significantly less fatigue life, at this stage of the corroded sample, significantly earlier into the region of accelerated fracture growth and steeper curves. The length of the crack 3 seconds before the failure, 乂1336730, is considered to represent the crack length measurement before the still believed sample is destroyed, and this result is also small for the corroded sample. Crack growth can also be interpreted as occurring incrementally and corresponding to a specific number of low cycle fatigues, while material elements before failure occur are broken. By assuming corrosion-induced embrittlement of the material, the fractured toughness of the corroded material will be small. The fracture toughness of the corroded material can be reduced by the measurement of the fracture toughness described in the next paragraph. The above considerations can explain the higher growth rate and the sharper crack growth during the accelerated crack growth phase. The reduced fracture toughness of the corroded material can account for the reduced fracture length at the time of failure, and the higher fracture growth rate at the stage of accelerating the fracture growth rate can also explain the reduced fatigue life for the corroded sample. The effects of corrosion and corrosion-induced hydrogen embrittlement on the fatigue and damage tolerance characteristics of 2024 aircraft aluminum alloy samples have been investigated. The experimental results show a significant reduction in the fatigue resistance and damage tolerance of the corroded material. The results obtained are discussed in terms of the synergistic effect of corrosion and corrosion-induced hydrogen embrittlement. These results show the need to account for the effects of pre-existing corrosion on material properties' for fatigue and damage tolerance analysis of parts containing corroded areas. Corrosion-induced hydrogen embrittlement of 2〇24 and 6013 alloys proposed by PV Petroyianis, Al. Th. Kermanidis, P. Papanikos and Sp. G. Pante 1 akis (Theoretical and Applied Fracture Mechanics, 2004) Published on April 1, pp. 1-3, vol. 173-183, which reveals the effect of corrosion on the mechanical properties of typical aircraft aluminum alloys. The result of this 42 1336730 shows that corrosion exposure causes a moderate decrease in the fall and final tensile stress. In addition, the recording extension is a significant reduction in damage and strain energy density, even after a short exposure time. The processing of the etched surface was found to restore the relief and ultimate tensile stress, however, the ductility of the material was not restored. After heat treatment at a temperature corresponding to the thermal adsorption of certain hydrogen capture sites, the latter gradually returns to the amount used for the uncorroded material. These findings show that the corrosion of the above alloys is related to the volume of hydrogen embrittlement. Tensile φ The significant decrease in ductility is related to the reduction in residual strength of the material being corroded. According to the concept of multiple spalling, a model is used to reduce the fracture toughness and residual strength, as well as the strain energy density obtained from the tensile test on corroded and uncorroded samples. It has been shown that strain energy density can be used to accurately predict the residual strength of corroded parts. In order to assess the structural integrity of aged aircraft parts, it is necessary to account for the effects of corrosion, catastrophic damage due to corrosion of the strength aluminum alloy and associated hydrogen embrittlement. When the corrosion interacts with other forms of damage such as single-fatigue cracks or multiple location damages, the effects of rot (4) hydrogen embrittlement can be attenuated. A number of committees and international conferences have been organized to carefully consider the degradation of materials in older aircraft, and one of the important issues is the rotten surname. However, the current consideration of the destructive structure of the rotten money is related to the existence of the rotten and the reduction of the load bearing capacity of the structural members of the surname. The importance of susceptibility-induced hydrogen embrittlement to structural integrity is not yet properly understood and is still underestimated. At present, the corrosion and gas damage mechanisms of Ming alloy are still unknown. The damage process involved 43 1336730 疋 occurs at the atomic level. The corrosion attack of aluminum alloys is attributed to the complex process of oxidation. However, 'many tests have shown that hydrogen produced during the etching process will diffuse into the interior of the material and cause concentration and capture of hydrogen at the preferred capture location, which is related to the alloy system. Most of the hydrogen embrittlement of aluminum alloys has been studied for the 7xxx series of A1 -Zn-Mg alloys. Metastable aluminum hydride has been considered to be the main cause of the fragile intergranular fracture of A Zn-Mg alloy which is cracked by stress corrosion in water vapor. The decohesion of grain boundaries containing sequestration money is another indication of intergranular fracture of these alloys. For example, hydrogen embrittlement of different aluminum alloy series such as 2χχχ, 6χχχ and 8χχχ is still underestimated and cannot be properly documented. In addition, it is not fully understood that 'hydrogen embrittlement can occur even in the absence of mechanical loading, that is, stress corrosion cracking is not necessary for hydrogen embrittlement. Corrosion-induced hydrogen embrittlement has been shown to be the main cause of the sharp degradation of toughness and ductility of the conventional 2024 and 6013 alloys, as well as the advanced 2091 and 8090 alloys. This degradation can be explained by quantifying argon release in the 2024 and 6013 alloys, as well as confirming different capture locations. These results have been applied to the treatment of corroded and uncorroded samples at temperatures corresponding to the hydrogen capture sites of each of the tested alloys. The fracture toughness of the corroded material is significantly reduced, and the local fracture toughness associated with the reduction in strain energy density must be evaluated. The method involving multiple spalling is very effective for the corrosive hydrogen embrittlement process with complex interactions. Therefore, it is recommended to check the effects of corrosion-induced hydrogen embrittlement on multi-site damage (MSD). The distance between the rivet holes of 44 1336730 can allow the local volume of the material to be embrittled. In order to quantify the effects of corrosion and corrosion-induced hydrogen embrittlement on the mechanical properties of aircraft aluminum alloys 2〇24 and 6013, a comprehensive experimental study was carried out. In addition to the tensile test, a residual strength test was performed using a dent and pre-generated fatigue (MSD) sample containing a row of double holes. Both the rotted and uncorroded samples were tested. A multiple spalling method is used to reduce the rupture and residual strength, as well as the strain energy density obtained from the tensile and uncorrupted sample tensile force tests, which are related to each other. The above experimental results can be confirmed using a wide range of fracture analysis (fract〇grapgic analysis). The effect of undamaged corrosion on the mechanical properties of aircraft aluminum alloys 2〇24 and 6013 was experimentally studied. The following conclusions were obtained: Corrosion-induced degradation of mechanical properties gradually occurred with exposure time. Tensile ductility is reduced exponentially to a fairly low final value. In order to interpret this result, it is necessary to use a multiple spalling method to reduce the gap between the damage process occurring at the microscopic level and the macroscopic mechanical properties of the material. Mechanically removes the corroded area, which has recovered to the most '-, tensile strength, but does not restore tensile ductility, where the latter can only recover after heat treatment of the alloy at a temperature corresponding to hydrogen capture. Thus, it means that the corrosion of the alloy to be tested is related to hydrogen embrittlement. The fracture toughness of the corroded material is significantly reduced, and it is necessary to evaluate the local fracture toughness associated with the reduction of the amount and degree. Using the strain energy density reduction measured according to the tensile test, the residual strength of the structural parts due to corrosion-induced hydrogen embrittlement was evaluated at 45 α336730. Known as Oriani, Richard A, Hirth, John Ρ· and Smialowski,

"Hydrogen Degradation of Ferroalloys" edited by Michael et al. (Miam Andrew Publishing/Noyes, 1985, p.900, ISBN 0-8155-1027-6) » which provides hydrogen metal interactions, mechanical considerations, and degradation of mechanical properties Important comments on the basics such as phenomena. Hydrogen degradation of structural materials is a serious problem that has gradually gained attention over the past fifty years. The ubiquity of hydrogen rot sources in aqueous solutions, the absorption of wet and contaminating hydrocarbons into pipelines, and the contaminants in the melting process contribute to the importance of this problem. Known by J. Burke, A. Jickels, and P. Maulik et al., "The Effect of Hydrogen on the Structure and Properties of Fe-Ni-Cr Vostian Iron" (Proceedings of an International Conference. Moran, Wyoming, 1976, Pp. 102-115), which points out the ductile loss in the Worthian iron steel associated with the adsorption of hydrogen by gas or electrolysis. Although the sensitivity of this material is less than that of ferrite iron and 麻田散铁钢, the mechanical properties are greatly deteriorated under the condition that the argon hydrogen concentration is absorbed. This has a very obvious dark indication for material use. Moreover, the clear association between the rupture of some types of stresses and the changes in hydrogen-induced structures and properties has increased the interest in understanding the basic mechanisms of gas embrittlement in these materials. The hydrogen embrittlement of Worthfield Iron and Steel can be divided into two types: (1) high hydrogen fugacity, low diffusivity (also low) and Worthite iron stability, resulting in serious internal Should change 46, 1336730, spontaneously converted into α and ε Ma Tian loose iron, and a wide range of intergranular and rupture across the grain surface; and (2) combination of components, temperature and fugacity, can make hydrogen absorb , but not accompanied by significant structural changes. Known by Shimomura, J. 'imanada, Τ· “Decomposition of Carbides in 2-l/4Cr-lMo Steel during Hydrogen Invasion” (Scripta

Metallurgica, 1985, Vol. 12, No. 19, pp. 1507 to 1511, which reveals resistance to hydrogen attack in 2.25Cr-lMo steel, which can be significantly improved by reducing Si content, and, in addition, carbides The chemical properties are based on the observation that the Si content seriously affects the composition and crystal structure of the carbide, and the influence of Si on hydrogen attack has been explained. The document also discloses a description of changes in the chemistry of carbides that occur during hydrogen attack and correlates them with the deterioration of mechanical properties in 2.25Cr-lMo steels having different Si contents. Known by R. Kot's “Hydrogen Invasion, Detection, Evaluation and Estimation” (2001, Asia Pacific Conference on Non-Destructive Testing), this document provides detection and assessment of hydrogen attack in steel. An overview of the method of estimation. Equipment that comes into contact with & high temperatures and pressures may suffer from hydrogen damage - thermal hydrogen attack. Argon argon is easily diffused in the steel, and cracks may be caused by the formation of CH44 & in the internal voids of the metal at high temperature and high pressure. This can lead to cracks in the grain boundaries and loss of strength to decarburization, which can make the material unreliable or dangerous. A complete weakening of steel damaged by hydrogen can be used to quantify the degree of degradation of the mechanical properties of the material. By understanding this, the residual life of the affected machinery can be estimated. Hydrogen has a variety of different detrimental effects on metals. Metallic hydrogen 47 1336730 Initiated degradation, caused by exposure to the atmosphere where hydrogen is absorbed into the material' and results in a decrease in its mechanical properties. The severity of hydrogen damage is related to the following factors: the source of hydrogen—external (gas V internal (dissolved); exposure time; temperature and pressure; there are solutions or solvents that may react with metals (eg, acidic solutions); Alloy type and its manufacturing method; amount of fracture in metal; treatment of exposed surface (barrier layer, for example, oxide layer as hydrogen permeation barrier on metal); final treatment of metal surface (eg. zinc-nickel plating); Method; and/or the degree of residual and applied stress. According to the combination and number of the above variables, hydrogen damage can be classified into: hydrogen embrittlement, hydride embrittlement, solid solution hardening, internal production (4), and

As shown in Figure 8, it can be subdivided into different damage processes. In the hydrogen attack mechanism and prevention, hydrogen forms a burning bubble in the material and reacts with carbon in the steel. The beryllion bubbles are formed on the grain boundaries and in the minute voids. Due to the expansion and combination of such bubbles, the pressure of the nail-burning increases, causing the gap to expand into cracks. The growth of cracks and voids can make the metal brittle and weak, and the crack will develop into a larger major crack. The degree of hydrogen attack is related to temperature, hydrogen partial pressure, stress level, exposure time, steel composition and structure. Hydrogen attack has been reported to occur in pure carbon steel, low alloy steel, and even in non-mirror steels operating at 473 Torr. Hydrogen attack is a major problem in refining furnaces where hydrogen and hydrocarbon vapors are operated up to 20 MPa and about 810 Torr. In order to prevent hydrogen attack from occurring at high temperatures and/or high pressures, an intermetallic alloy content is required. Cr, M〇, w, v, Ti, Nb, etc. are carbides forming halogens, which can be used in steel to provide the desired resistance. 48 『1336730 The Nelson curve for API 941 based on industrial experience, which provides general guidance on the selection of alloys. The alloy that is suitable for selection is shown as a curve to the right or above the temperature/hydrogen pressure coordinates, which represents the expected parameters of the operation. Heat treatment can affect the resistance of steel to hydrogen attack. For example, 2.2 5Cr-l Mo steel subjected to quenching and tempering has an increased sensitivity to hydrogen cracking due to the low resistance of the granulated iron and the bainitic structure to hydrogen damage. Heat treatment that may result in excessively high levels of strength may be avoided or used with care. Industrial experience has pointed out that post-weld heat treatment of Cr-Mo steel is helpful for resisting hydrogen attack during hydrogen operation. It is a common practice for manufacturers of hydrogen/hydrocarbon compound equipment to perform embrittlement tests on welding consumables and to store all "low hydrogen" electrodes in the hot "box" before starting production. Preheating regulations for low chrome steel can result in weld cracking caused by shrinking hydrogen during manufacturing. Proper inspection, quality control, good design, and a reputable manufacturer are necessary to ensure that the final vessel or reactor is resistant to argon attack. Hydrogen attack is caused by exposing the steel to a hydrogen environment. The severity of the damage is related to exposure time, temperature, hydrogen partial pressure, stress level, steel composition and structure. In order to avoid/prevent hydrogen attack, it is necessary to use a 70-form stable stable Weisaki. It should be small (applied to heat treatment to avoid the formation of structures with very low resistance to hydrogen attack (Mita iron, toughened iron). During the manufacturing process of hydrogen and hydrocarbon handling equipment, proper inspection and Quality management system. The hydrogen of the steel used in the equipment is not damaged or damaged, and should be used for hydrogen attack testing, etc. 49 1336730 Known Takumi Terachi, Nobuo Totsuka, Takuyo Yamada '

The effects of dissolved hydrogen on the oxide film on alloy 600 formed on the main water in a pressurized water reactor by Tomokazu Nakumi, Hiroshi Deguchi, Masaki Horiuchi, and Masato Oshitani (Nuclear Science and Technology Journal, 2003, No. 7) Volume 40, pp. 509-516), which discloses the relationship between the main water stress corrosion cracking (PWSCC) in the alloy 600 and the dissolved hydrogen content in the main water of the pressurized water reactor (PWR). Research result. Therefore, using a grazing X-ray diffractometer (GIXRD) 'Scanning Electron Microscope (SEM)' and a transmission electron microscope (TEM), it is formed under four different DH conditions in the simulated main water of the PWR. Structural analysis of oxides. In particular, in order to perform accurate analysis of this thin oxide film, synchrotron radiation of Spring-8 was used. The oxide film is mainly formed by nickel oxide in the absence of hydrogen. On the other hand, a needle-like oxide is formed at a DH of 1 · 〇 ppm. In the environment of 2.75 ppm of DH, the oxide film has a thin spinel structure. Based on these results and phase diagram considerations, the condition 'n near DH of LOppm corresponds to the boundary between the stabilized NiO and the spinel oxide, and also corresponds to the peak range of PWSCC sensitivity. This result shows that the boundary between N 〇 and spinel oxide may affect the sensitivity of scc. It is known that P. M_ Scott proposed "internal oxidation which may be explained as intergranular stress corrosion cracking of alloy 6〇〇 in pwr" (on the environmental degradation of materials in nuclear energy systems/water reactors) The Ninth International Conference), which provides research on the internal oxidation mechanism in pressurized water reactors. Scott and Le Calvar first proposed a possible mechanism for internal oxidation to intergranular stress corrosion cracking (IGSCC) in hydrogenated pWR aqua regia in 1993. Since then, at 13 1336730, several experimental studies have been tried to test this hypothesis. Detailed analysis of the primary and secondary cracks in the alloy 6〇〇 has been carried out using secondary ion mass spectrometry (SIMS) and analytical transmission electron microscopy (ATEM), and preliminary results have been published. Some arguments are revealed regarding the applicability of the internal oxidation mechanism at typical PWR operating temperatures and corrosion potentials. The apparent reaction rate of oxygen intergranular diffusion in a nickel-based alloy, and the observed rate of internal oxidation cracking and thermodynamic requirements at or below the corrosion % of the Ni/Ni〇 redox reaction potential, resulting in two Rate reconciliation causes a special problem. If the mechanism is used to interpret the secondary side steam generator tube IGA/IGS (X, then the latter argument is particularly important. The second objective is to describe the intergranular internal oxidative rupture observed at high temperatures. The type of known situation, in order to provide other X (four) reference points in this meeting, the topic of this meeting is a detailed examination of the crack in the contract produced under the real or prototype conditions. Known by VS Sinyavsky, VD Valkov and VD Kalinin Temple, "Corrosion and Protection of Ming Alloys" (MQseQw, Metai Ring 1986), this document reveals that Ming alloys suffer from different kinds depending on factors such as king's conditions and alloy composition. Corrosion. These types of corrosion include: corrosion cracking, intergranular corrosion, and (4) - some copper-containing alloys are susceptible to intergranular corrosion. Such corrosion sometimes occurs in aluminum alloys containing magnesium and niobium. Due to improper heat treatment, and sometimes (d) for extended exposure to sunlight in many environments such as seawater, ocean and industrial atmosphere, 51 1336730 The intergranular rot of the grain. The theory of intergranular corrosion is considered: during the artificial aging of the alloy, or in the temperature range between 9〇〇c and 27〇〇c, 4 other heat treatments produced during the heat treatment period (4) M_eu will destroy and produce a main precipitate on the boundary of 曰θ. The composition of this precipitate is very close to the metal compound CuAl2. Thus, a copper depletion region will be caused near the boundary. In the B granule, the metal compound is only The degree of precipitation is small, and therefore, the amount of copper consumed in the region where the solid solution leaves the boundary is relatively small. Due to the thermal action in the above temperature range, the surface of the alloy may not be from an electrochemical point of view. It is considered to be homogeneous and homogenous. The potential difference between grain boundaries and grains can be as high as 100 mV, which eventually leads to electrochemical corrosion. In general, appropriate potential can be provided on the entire surface by appropriate heat treatment. Distribution, to prevent intergranular corrosion of aluminum alloy. The correct heat treatment is to make the alloy more uniform and homogenous, and the more copper is converted into a solid solution, and the solid solution can be It is fixed by rapid quenching treatment. When duralumin is quenched in cold water (4〇〇c) from 48〇 to 5〇〇〇c • f, it will have the best when it is naturally aged. Corrosion resistance. When the alloy is affected by both corrosive environment and static tensile stress, corrosion cracking occurs. The stress can be external and internal stress. Some aluminum alloys are prone to stress corrosion cracking. The alloy is damaged by such harmful corrosion. Sensitivity is related to metal structure, stress size and characteristics, and corrosive environment. Selective attack on the corrosive environment of the alloy helps to produce cracking of the rot. Stripping corrosion is a special kind of subsurface corrosion, which is mainly Parallel 52 1336730 produces a '胄 deformation during deformation of the semi-finished product, and is accompanied by crack formation in this direction, the fall of individual metal particles, or complete destruction of the sample and part. Such corrosion can occur along grain boundaries, or from the deformation boundaries of dendritic cells, as well as across grains. Peeling Corrosion is generally a typical representation of a semi-finished product. In some exceptional cases, this can be observed in conventional castings with directional liquefaction, e.g., in a w_Mg_Li alloy having a high manganese content. Corrosion spalling can be attributed to the following factors: special structural state, orientation of the second phase, solid solution crystallization in this deformation direction, high content of alloying elements or impurities and their uneven distribution, internal stress, and: corrosion The special physical and chemical state of the surface related to the sexual environment. Therefore, the corrosion resistance of aluminum alloys at work can be determined by the following criteria: surface fineness, internal compressive (favorable) stress, and the special structure of the alloy near the surface, which is produced by special igniting conditions. . Under optimal conditions, the ultrasonic shock applied to the surface of the aluminum alloy can combine all of the above suitable factors. The corrosion of aluminum and its alloys (Mosc (10), Metallurgia, 1967) is known from V.V. Gerasimov. This document reveals that the electrochemical properties and corrosion resistance of aluminum are closely related to the purity of metals. The resistance of aluminum alloys is related to the properties and quantity of alizarin. At temperatures below the sail, pure aluminum has the greatest resistance to corrosion. In water and in a neutral environment that does not contain active ions (e.g., self-priming), the static potential of pure aluminum corresponds to the -passive region. Therefore, under the conditions of money, pure resistance will be quite high. Alloying from aluminum changes the kinetics of the anode treatment. The static potential of the Ming with 1% iron content 53 『1336730 corresponds to this passive area. Thus, a relatively low corrosion rate of such alloys can be determined, although this rate is still more variable than that of pure aluminum. In a 3% sodium chloride solution, the corrosion rate of the alloy will increase from 〇. 004%' in proportion to the iron content. The alloy of Ming and copper will make the kinetics of the anodizing treatment (aluminum alloy solution) louder than in the case of iron. When the copper content is increased to 〇. 〇丨%, a slight increase in the corrosion rate in the 3% vaporized sodium solution can be observed. As the copper content increases further, the corrosion process is significantly enhanced. Alloys with nickel and nickel will excessively reduce hydrogen and oxygen. Due to the introduction of nickel, the acceleration of the cathode treatment will increase the static potential of the alloy. The standard potential of the alloy containing 0.2% nickel corresponds to this passive region, and the corrosion rate in this case is very low. With a nickel content of more than 0.6%, the static potential corresponds to an overpassive region, and this corrosion rate naturally increases. Therefore, the content of alloying elements up to 1% for aluminum has the greatest influence on the kinetics of electrode treatment. When alloys are formed with iron, copper or nickel, the aluminum alloy contains metal compounds of these elements. The electrode potential of the metal compound is more positive than the static potential of aluminum, so it is used as a cathode in an aluminum alloy. A total of 1 to 2% of manganese, zinc, magnesium and antimony does not enhance the corrosion process. When the zinc content is increased to 25%, the static potential of the alloy is converted to the cathode direction in a neutral and acidic environment. In fact, the static potential of the alloy is not affected by a further increase in zinc content. Adding 〇. 16% zinc to aluminum has only a small effect on the rate of cathode treatment. Therefore, the zinc alloy with 2·〇5% does not increase, but even slightly reduces the corrosion rate. 54 『1336730 The magnesium content of 5% does not significantly increase the corrosion of aluminum. In a neutral or acidic environment, when the aluminum-magnesium alloy is formed, the static potential is reduced. Such a result also occurs in the case of alloying with lithium. In a neutral environment, in fact, the static potential of aluminum is not affected by Jane; in an acidic environment, it increases. In fact, the smash in the solid solution has no effect on the etched corrosion. However, the ruthenium metal compound may have a local cathode and accelerate corrosion. It should be known that 矽 seems to significantly increase aluminum

The protective properties of the oxide film on the surface are due to the very high corrosion resistance of the bismuth aluminum alloy. In an acidic environment, the sodium content from 〇.035 to 〇 〇 78% = is important for aluminum resistance. The maximum sodium content of aluminum containing 〇 3 to 钝. blunt iron impurities should be between 〇 2 and 〇. If it exists in the inscription, it will strengthen the intergranular rot. 〇 0 · 0 8 % of the calcium content will slightly reduce the resistance of commercial aluminum in the neutral environment. . .5 to L0. The opportunity is significantly increased in the 0.5 to n test solution:

Corrosion (equivalent concentration of η table wrong liquid). When cut, the texture is particularly harmful. The alloy of Ming and about can inhibit the adverse effects of the pin, and the influence on it is small. Chin content exceeds ruggedness in acid = eclipse. However, cobalt, Ming, silver, and hunger all have adverse effects. For example, a 4th-year-old alloy is completely destroyed after the atmosphere of the relative degree (10) is deleted. By effectively operating the Ag2M metallization to the cathode, a high rate of decay can be achieved. In - some love. Things do not have any effect on tin, tin, etc., but sometimes "go some:, strong corrosion. It will improve the corrosion resistance of aluminum. ', θ 55 1336730 even a small amount of mercury 'will lead to aluminum mercury Purification, metal surface de-purification' and increased metal dissolution rate. The mercury-containing protective device has a sufficient negative potential, so in fact, it cannot be passivated over time. Alloy Scenery > Static Potential and Corrosion Resistance and PH Environmental dependence. In an alkaline environment, pure aluminum and most aluminum alloys are not resistant. Under such circumstances, alloys doped with 〇·5% magnesium have the lowest corrosion rate. When magnesium forms an alloy, an oxide film is formed on the surface of the metal. The film contains barium hydroxide, which is insoluble in the alkali solution. In the diluted alkali solution, the alloy resistance increases with the magnesium content. In the concentrated alkali solution, Magnesium does not increase the resistance of aluminum. Magnesium and manganese alloys can increase the resistance to ammonia. In the acyl water containing ammonia, 99 to 99.5% aluminum and 1.25% manganese or 3% magnesium aluminum alloy, can Anti-corrosion. In non-oxidizing acid, strontium can be enhanced and calcium can inhibit the resistance of aluminum. Zinc and short have a bad effect 'Magnesium and tin can enhance the resistance to rot. In the homogenous ^ gold towel' 1% (four) It does not weaken the purity in nitric acid. In the alloys with different composition, '1% _ can (4) weaken the resistance in 65% nitric acid. 1% content of copper, even if it is not completely dissolved in aluminum, It is also able to significantly enhance the resistance in 25% of the acid. In the 5/. and 1〇/❹ hydrogen acid, 99. 96% of the Ming and the ο"% town. Kim’s is quite resistant to the surname. In these cases, the rate of decay was not more than 3 to 5 g/ffl2 for 4 days, and the individual corrosion rates were 352 and 7780 g/ra2 days. Impurities and alloying elements are very corrosive to pores in g and its alloys. The shirt of the person is ringing. In 99.99% of the Ming, it is difficult to observe the corrosion in fresh water. 56;,: In the 99.5 to 99.8% of the Ming, in the week, the depth of the decay may reach 0.3. Ming purity decreased from 99 99% to the increase in the rate of cathodic treatment in the oxygen ionization zone, as well as the rate of diffusion current and hydrogen ion discharge. This will make the hole corrosion. The action of the local cathode can barely localize the corrosion. The higher the content of iron and copper, the greater the number and depth of the hole a. The corrosive voids are typically oriented to correspond to the direction of rolling of the metal compound arrangement. It is also possible to observe hole corrosion in the scratched area where metal compounds are present. When the aluminum surface is treated with boiling water, it will recover in the area damaged for some reason - the protective film. Such treatment enhances the resistance of the alloy to void corrosion. Other surface treatments, such as degreasing after rolling, chemical polishing in a mixture of phosphoric acid and nitric acid in a (10) test, have no effect on the resistance of the 110 alloy in the 53-to-hund steamed tooth water. . Surface polishing in the chloride 'valley' reduces corrosion loss. In a 0. 0 (Π-1· 0-n concentration of potassium sulfate solution, the polished (four) is actually and will be rotted. The chemical polishing flt* is sufficient in an atmosphere of 87 % RH, making 99.5% of the The amount of corrosion is reduced by a factor of 5. Aluminum "gold surface treatment will affect its tendency to corrode. Because of the name of the step, the 2S and 3S alloys (in the processing alloy used in the process are now labeled 1 (10) and 3003 respectively) The depth of the hole above is increased by 10 to 50 times when tested in fresh water. Plastic deformation will disrupt the integrity of the inter-grain between the grains, thus increasing the resistance of the iron-and-nickel-containing imprint to the intergranular rot. By using a lower heating temperature before bonfire and 57 aging, the internal adsorption between grains can be reduced 'or the solid solution decomposition at the grain boundary. Under the combined effect of the corrosive environment and mechanical stress, some Aluminum alloys (such as alloys doped with magnesium or magnesium zinc) are subject to a special form of attack, typically referred to as corrosion cracking or stress corrosion. This form of attack is usually observed in environments containing vapors. Corrosion cracking of aluminum alloy can The precipitation of Mg2Al3 at the grain boundary is explained by the metal compound phase. This metal compound is found by metallographic and electron microscopic studies on the grain boundary of the magnesium-doped aluminum alloy which is corroded by corrosion. The mechanical stress will be in the metal. The dents and cracks in the compound which are invisible to ordinary microscopes are promoted to promote the penetration of the corrosive environment into the point phase, and the decomposition of this phase is strengthened. In addition, the tensile stress can promote the penetration of the 10,000 phases along the boundary of the crystal. Corrosion cracking of the magnesium-doped aluminum alloy The process is described as follows: The phase of the crystal boundary is not passivated in the vapor solution and is strongly decomposed. The metal compound may be decomposed and formed during the manufacture and processing of the alloy or under the influence of tensile stress. Cracks that are not visible to ordinary microscopes can lead to the formation of concentrates or sinks of zinc metal compounds. Therefore, this process will strongly propagate deep into the metal. The degassing or cathodic polarization of the environment will change the potential in the cathode direction. And weaken the decomposition of the stone phase and the corrosion cracking process. Anodic polarization or with more precious metals (copper, stainless steel) Touch, which increases the rate of decomposition of the phase (which is not passivated in the chloride), thus enhancing corrosion cracking. This corrosion cracking process is the fastest when the alloy surface is subjected to acid or etching. Surface polishing increases the alloy. By the time before the destruction, by increasing the pH from 0 to 6, the life of the sample 58 before the destruction will also increase. The same copper (four) alloy is less susceptible to rot silver than the magnesium-copper double alloy. The effect of rupture. Forming alloy with 0:5-U zinc can enhance the rot of the alloy containing t 嶋 抵 抵 抵 U U U U U U U U U U U U U U U U U U U U U U U U U U U U U U U U U U U U U U U U U U U U U U U U U U U U U U U U U U U U U U U U U U Increased. Under the effect of the rot environment and the alternating load, the alloy may be damaged due to the fatigue of the rot. Because of the rupture of the rot, the vapor will accelerate the destruction of the alloy. In the 3% sodium chloride solution, the fatigue limit of the 2024 alloy was 3. 5 kg / mm 2 operation 1 〇 7 times. In closed systems, inhibitors are widely used to protect metals and alloys against corrosion. Some oxidizing agents (for example, chromate and dichromate) are used as a stagnation inhibitor in a neutral environment! (passivating agent). At low temperatures, complex salts can be used to protect aluminum and its alloys against corrosion in neutral, alkaline and weakly acidic environments. If 〇 5_1〇g/1 sodium chromate or chromic acid is added to water containing up to 50-l〇〇mg/1 salt, the corrosion rate of aluminum and its alloys will be greatly reduced. With higher salt concentrations, especially copper, the chromic acid protection properties are reduced and voiding can occur. Other compounds can be used as inhibitors to protect the aluminum portion of the cooling system. Therefore, by adding 3% sodium nitrate, 3% 3% sodium phosphate, and 3% phosphoric acid-sodium salt to 8 含有 containing 35 mg/l of chloride. (: River water can reduce the corrosion rate by 2 to 3 times. Adding 〇· 〇3% sodium nitrate and sodium citrate, 3% sodium benzoate can reduce corrosion by 6 to 8 times. GV Akimov confirms the electrification of hard aluminum Visual protection. Visual observation shows that the 4m long hard plate on the zinc-fluster is not damaged by the seawater test. The cathodic polarization has a potential of -G.8V across the vaporized silver electrode. , can protect the unique sea seal for six h in the material, the hard hull can be protected from corrosion by the protection device. The beta magnesium protection device is evenly located at the bottom of the ship and fixed to the B by galvanized steel bolts.埽 塑胶 塑胶 塑胶 。 。 。 nik nik nik nik nik nik nik nik nik nik nik nik nik nik nik nik nik nik nik nik nik nik nik nik nik nik nik nik nik nik nik nik nik nik nik nik nik nik nik nik nik nik nik nik nik nik nik nik nik nik nik nik nik nik nik nik nik nik nik This document reveals that in the case of 纟&, the corrosion resistance of Alloy 26 can be significantly enhanced by the application of a protective coating. For aluminum alloys, an oxide film is formed by oxidation and anodization, "- General practice. Anodization is greatly increased And the resistance of the alloy to the industrial atmosphere. The preferred oxide film for aluminum is an oxide film having a thickness of 0.025 - 0. 〇 15 mm and anodized by sulfuric acid and oxalic acid. Under the condition of Li gasification, it can be forbidden for one year. It can be treated in high temperature water or aqueous solution to produce a protective oxide film on the surface of aluminum alloy. It can be achieved by plating pure aluminum. High resistance to aluminum alloys in seawater. This coating not only isolates the alloy from corrosive environments, but also electrochemically protects the alloy. To protect the aluminum alloy from corrosion, it can also be used in water, Acid, weakly alkaline detergents, and urban air are exceptionally durable. Bitumen, polymer and paint coatings and greases can be used to protect aluminum and its alloys from rot in the atmosphere and soil. Known ND Tomashov and GP Chernova's "Corrosion Theory and Corrosion Resistant Structural Alloys" (M〇sc〇w, MetaUurgia, reveals that when (4) is in contact with high-field M gas or non-electrolyte: =: It is the representative of metal damage. When the phenomenon occurs, the original reaction 'is like electrochemical corrosion. In the metal teaching, the thirsty wheel jet engine, the rocket engine, the power generation, the details in the I, the parts... The gas produced during the metallurgical operation is rotted.

The ability of metals to resist the invasion of high temperature gases is called thermal resistance. Another important property of metals at elevated temperatures is the high temperature strength, which can be used to define the ability of the material to maintain good mechanical properties under these conditions. Metals can be heat resistant' but do not have good high temperature strength (for example, in _ to 450% of the alloy). At _ to 7〇〇〇c, Idle Steel can be hot, but it is not strong at rfj.

The interaction between metal and oxygen (metal oxidation) occurs according to the following chemical formula: Me+02=Me02. The oxygen molecules that reach the metal are attached to (ie, captured) by the metal surface. Oxygen adsorption in metals is generally expressed in the following manner: This physical adsorption occurs on a clean surface whereby the bond between the oxygen atoms and the molecules is weakened. The molecules separate and the oxygen atoms attract electrons away from the metal atoms. A chemisorption phase is created when electrons drift toward oxygen while forming a nucleus of 0-2 ions equal to the metal oxygen compound (oxide). A product of the interaction of oxygen with metal (oxide) that provides a chemically active oxide film on the surface. Depending on the thickness, the film on the metal can be classified into: thin (invisible) thickness below 40 nm; average (visible in tempered color) - thickness of 40 to 500 mn; thickness (visible) - thickness exceeding 5〇〇nm. For example, in the case of aluminum: after a few days in dry air, the film is 10 nm; 61 '1336730 after 600 ° C and 60 hours, the film is 2 〇〇 nm; after anodization, the film becomes 3 It is thicker than 3〇〇々111. For metals and alloys, the gas rot # rate is subject to external factors such as composition, gas environment force and speed, temperature and heating conditions, and internal factors such as alloy properties, chemical and phase composition, mechanical stress and deformation. influences.

The protective properties of the oxide film are substantially related to the properties and composition of the alloy. Chromium, aluminum and niobium can significantly slow down the oxidation process of steel, and this phenomenon can occur due to the thin mold of the protective properties. Deformation of the metal during heating can cause the film to break, thereby increasing the rate of oxidation. The initial deformation is only below the recrystallization temperature and has a small effect on the oxidation rate. To achieve gas corrosion protection, heat resistant alloys, protective gases, and protective coatings can be used.

Known by F. Todt, "Corrosion and Corrosion Protection" (Khimiya, Leningrad, 1967), the document reveals that the electrochemical corrosion process is a combination of two coupling reactions - anode reaction (oxidation) Me = Mez + + ze; Cathodic reaction (recovery) D + ze = (Dze); where D is a depolarizer (oxidant) which attracts z electrons (ze) which are released due to the anode reaction (metal ionization). A schematic of the electrochemical decay process is shown in Figure 9. The surface of the actual alloy is always heterogeneous, that is, the surface of the bismuth metal with different potentials differs not only in micro irregularities (grain boundaries, impurities) but also in submicron irregularities (crystal structure). The imperfections, the alien atoms in the 62 lattice, etc.) are also different. This results in localization of the anode and cathode treatments and results in localized corrosion (e. g., void formation) - the theory of operation of the microbattery elements under electrochemical corrosion conditions. SUMMARY OF THE INVENTION The present invention is directed to a method and algorithm for improving metal properties with ultrasonic shock and combating degradation and suppression of metals. The method and algorithm can solve the problem of deteriorating metal characteristics during the extended work under the influence of external forces, thermal fluctuations and unfavorable environmental factors. The present invention also relates to combating (i.e., preventing) and inhibiting the risk of material damage due to undue changes in performance over time. This type of problem occurs because it is caused by the known structural conditions associated with the degradation of the metal environment, which causes the initial structural damage of the material. In each particular case, known methods of combating metal degradation cover a wide range of techniques, from melting, casting, welding and metallurgical alloys during application of the coating, to various heat treatments and effects on the surface. The present invention provides a novel multi-functional method and algorithm to deal with degradation problems in all of the above scenarios. Hereinafter, methods and algorithms for processing an affected object will be described in detail. Before and after the technical action, the reaction of the metal boundary layer to its own characteristics and conditions substantially affects the characteristics of the subsurface layer. These features, whether alone or in combination with surface features, define the method. effectiveness. The efficiency of this method and / or algorithm means the degree of influence on the material performance, which is due to the specified characteristics of the material and the structural changes of the structure 'stress deformation state of the structure, and the ability of the material to resist external forces, temperature changes and environmental effects, etc. The reason for the factors "Therefore, the method and / or algorithm of the present invention 63 1336730 points out the surface and the material under the surface are two independent but related entities, and, in this paper, provide a method to increase the object against the possible The ability to degrade the performance of its performance. Therefore, the requirements of the treated surface and the conditions of the underlying material can determine the technical characteristics of the surface and material of the affected object as the two related but independent technical efficiency criteria. Thus, the following describes in detail the methods and/or algorithms for ultrasonic shock, as well as the versatility and special application variants in the engineering field that have different causes of degradation in object material properties. The method and/or algorithm of the present invention also addresses the task of improving metal degradation resistance. The method and/or algorithm begins to organize and control the flexibility and strong normalization phase of the ultrasonic shock defined by this task, and the technique for obtaining the practical application is effective to suppress degradation (the super-wave is used according to the method of the present invention) Impact control). "Flexibility" is about the phase and number of ultrasonic shocks, which corresponds to this task and directly manages the predetermined or experimentally established state of the material, when the impact resistance of the material is confirmed, and the material (4) In the treated area, when the minimum amount of impact resistance is generated according to the impact phase, the maximum possible strengthening (plastic deformation) is caused while maintaining the intermediate structural integrity of the material. The main stages of organizing and controlling the flexibility and strong normalization phase of ultrasonic shocks are as follows: The dynamic strength of the mass is evaluated in the context of the subsequent formation of an optimal intermediate structure on the surface of the object; ν is selected according to this limb/or H (4) Parameters and depth of ultrasonic impulse or strong phase; 64 1336730 In the context of suppressing the beginning of degradation process and preventing its possibility, the surface structure condition of the material and its repair (4) task definition of experimental or professional analysis; (according to this (four) method and Algorithm) normalizes the ultrasonic shock, for this: the experimental or professional choice of the strength and order of the influence of the material structure above and below the surface defined by the service; after maintaining the integrity and providing a special enhanced flexible phase of the intermediate structure of the surface material Parameters and sequences of force effects on the surface material structure of the mosquito during ultrasonic shock; preparation and consistent implementation of the method and/or algorithm of the present invention; experimental confirmation of the results to match the first experimental series of samples or simulations Technical tasks on the device; enter this result into a database; and/or form a material The stage of surface and subsurface properties is implemented according to the degree of use of ultrasonic shock control (selected by the above method) to implement the degradation suppression method and/or algorithm. [Embodiment] The present invention relates to a method of improving metal properties by ultrasonic shock and resisting degradation and suppression of metals. The method can deal with the problem of deteriorating metal characteristics during extended work under the influence of external forces, thermal fluctuations and adverse environmental factors. The present invention also relates to combating (preventing) and suppressing the risk of material damage due to undue changes in performance over time. This type of problem occurs because of the initial structural damage of the material caused by the known conditions associated with the environmental degradation of the metal. Figure 88 shows the environmental degradation of different kinds of metals. Environmental degradation of metals 65 1336730

::: Poison: Hydrogen damage ' Liquid metal attack, and light damage. Corrosion Guangshui (four) Husband and high temperature rot #. Aqueous solutions can be attacked by general, local or localized corrosion. Local attack of the aqueous solution may include galvanized money 'fracture rot #, depression, intergranular corrosion, selective leaching, erosion of corrosion, or rot * rupture. High temperature _ including metal Weihua is corroded by wire. Oxidation of metals may include: hydrogen embrittlement, hydrogen bubbles, flakes, fisheyes, and pulverization of Wei's intrusion into hydrogen (including) loss of force ductility: hydrogen stress cracking, hydrogen environment embrittlement' or hydrogen formation Embrittlement. Liquid: Invasion can include liquid metal embrittlement, grain boundary infiltration, and/or liquid metal corrosion. Radiation damage can include radiation growth, void expansion, radiation enhanced creep, and/or radiation enhancement and embrittlement.

* Known methods for combating metal degradation in each special esthetic range cover a wide range of technologies, from metallurgical phase 炫 during stenciling, casting, splicing and application of coatings to various heat treatments and effects on the surface . The present invention provides a novel approach to cope with the degradation problems of all of the above scenarios. Hereinafter, a method of processing an affected object will be described in detail. Before and after this technique, the reaction of the metal boundary layer to this effect and its characteristics and conditions substantially affects the characteristics of the subsurface layer, which together with or in combination with the surface features define the technical efficiency of this process. The technical efficiency of this treatment method means the degree of influence on the material properties, which is due to the specified characteristics of the material and the specified changes in the structure, the stress deformation of the structure, and the ability of the material to resist external forces, temperature changes and environmental effects. Thus, the method of the present invention points out that the surface and underlying materials are two separate but related entities, and an ability to increase the resistance of the object to 66 1336730 causing its own performance degradation is provided herein. The requirements for the treated surface and the conditions of the underlying material determine the technical characteristics of the surface of the affected object and its material as two related but independent technical efficiency criteria for this method. Thus, the following describes in detail the method of ultrasonic shock, as well as variations in versatility and special applications in the engineering field with different causes of degradation in the material properties of the object. The method and/or algorithm of the present invention also addresses the task of improving metal degradation resistance. This method begins to organize and control the flexibility and strong normalization phases of the ultrasonic shock defined by this task, and obtains the technical efficiency of the actual application situation to suppress degradation (the ultrasonic shock control is used according to the method of the present invention). "Flexibility" is the phase and parameters of the ultrasonic shock, which corresponds to this task and directly manages the predetermined or experimentally established state of the material, when the impact resistance of the material is confirmed, and when the material is processed In the region, when a certain minimum amount of impact resistance is generated according to the impact phase, the maximum possible reinforcement (plastic deformation) is caused while maintaining the intermediate structural integrity of the material to be treated. The main stages of organizing and controlling the flexibility and strong normalization phase of ultrasonic shock include the following: Evaluating the dynamic strength of the material in the context of the subsequent formation of the optimal intermediate structure on the surface of the object; according to this method 'selecting to control the ultrasonic shock Parameters and depths of flexible or strong phase; experimental or professional analysis of material surface structure conditions and their modified task definitions in the context of inhibiting the initiation of degradation processes and preventing their possibility; 67 1336730 (according to this control method) normalized defined The influence of the material structure on the top and bottom of the surface is the professional choice for this task; the strength and sequence of the experiment or the maintenance of the temperability and the provision of the surface material flexible phase 桉 ^ γ negative intermediate structure of the special reinforcement of the soft Parameters and sequence of force effects during ultrasonic shock; '& surface material is structurally prepared and consistently implemented in accordance with the method of the present invention;

The experimental series of samples or modules are experimentally confirmed to match the technical tasks on the first simulator; input the results to a database; and/or at the stage of forming the surface and subsurface characteristics of the material, according to the use of ultrasonic shock The degree of control (selected by the above method) is carried out to implement this degradation suppression method.

Ultrasonic shock is accompanied by two actions: (1) the movement of the oscillating system under the elastic restoring force caused by the oscillating system bounced back to the surface being treated; and (2) the ultrasonic wave connected to the oscillating system end of a dent Concussion, as shown in the examples in Figures 34 and 35. As shown, the basic tool includes at least one indenter 103, a waveguide 102, a magnetostrictive sensor 101 (having a housing 107 as a water-cooling housing), a spring 106, and a handle having a handle. Toolbox 105. The magnetostrictive sensor 1〇1, the waveguide 1〇2, the indenter 1〇3, the toolbox 105, the spring 106, and the housing 107 of the sensor form the oscillation system (OS), which has a structural structure fixed thereto Processing structure. The following is a description of the condensing system used in the specification and graphics of the present invention: OS_ Zhensheng System 68 1336730 0SE - oscillating system end TS attached to the dent handle - processed surface UI - ultrasonic shock vos - oscillation of the oscillating system Velocity V0SE—0SE The oscillating velocity vr at the ultrasonic frequency—in a certain period ′ the sum of vQS and Vqse and the combined oscillating velocity of SE

M〇s - the quality of the shock fish system Pini. The frequency of a supersonic shock force pulse fos_0S oscillation frequency (2〇〇Hz) f0SE—0SE oscillation movement frequency (27〇〇〇Hz)

Displacement amplitude of oscillating movement of Aos_OS (〇 3mm) Displacement amplitude of oscillating movement of A0SE—0SE (〇. 〇3 ugly) Ψ—Phase of ultrasonic shock Lu F_0S against TS squeeze _ force

Figure 36 shows the plastic deformation distribution during the ultrasonic shock of the present invention. The average statistical ultrasonic shock impacts the three time intervals on the object (not labeled a'b|^e in Figure 36) to define the plastic deformation distribution in the material being processed during each impact event. Strength. These intervals include: (a) at an increasing frequency greater than the frequency of the ultrasonic sensor, the dent is in the narrowed gap between the surface to be treated and the seismic edge B. Mountain, the surplus system, and the non-tailed ridge Sheng, (8) Synchronization and phase continuous vibration L(c) in the system and system "shock system - dent _ treated surface" due to the shock system from the surface of the treated surface, as shown in Figure 37 'The damping of the dent is oscillated within the incremental gap of 69 1336730 between the treated surface and the end of the seismic system. When this happens, the rebound and impact of the oscillating system will occur randomly with respect to the ultrasonic oscillation at the output of the oscillating system (the carrier shock of the ultrasonic sensor), and a random pattern of phases is formed, as shown in the figure. The crime shown represents the beginning and end of each ultrasonic shock event, and its three time intervals, namely (a), (b) and (c). The speed of the oscillating system and the speed of the ultrasonic shock absorber of the oscillating system with the dent are randomly added, and the problem of dynamic over-loading occurs on the surface affected by the ultrasonic shock, and the intermediate structure of the material of the treated surface is exceeded. Dynamic strength limit. This will lead to the following situations: (a) the dispersion of impact energy on the surface damage caused by the collapse of the intermediate structure, and the unfavorable development of these damaged ia shapes under the influence of subsequent impacts; (b) the strength of the plastic deformation induced in the surface material and The reduction in depth and the resulting unfavorable compressive stress; and (c) the ultrasonic oscillating energy and the reduction of the ultrasonic stress wave in the material of the affected object; >. These factors make it difficult to control the quality of the ultrasonic shock treatment and reduce its technical efficiency, that is, the ability to consistently reproduce the predetermined structure, conditions and characteristics of the material to be processed at a predetermined depth of the surface. Metal degradation is accompanied by the collapse of intermediate structures that occur primarily in the surface layer; the dynamic strength of the surface material is defined by the surface deformation rate in the following relationship: V = 2iJ/pc, where σ is the dynamic at a particular load rate Tensile strength, Ρ is the material density 'c is the speed of sound or deformation propagation in the material, V is the speed of action before or after surface damage, and pc is resistance to this effect (power, sound, quasi-static). The 70" results are shown in the ultrasonic frequency range, and there is still room for preservation for increasing ultrasonic impact strength. Therefore, the amplitude of the ultrasonic oscillation and the frequency of 27 kHz have an oscillation speed of i5 m/sec. The critical speed under dynamic action on steel with a drop strength of 7 MPa is 34 m/sec. As a result, for the higher carrier frequency of ultrasonic shock, it is more practical to change to 8 kHz. However, this reserved space is very susceptible to external factors and environmental factors that may cause degradation of material properties during long periods of work. Therefore, using the developed method, the construction and maintenance of the critical load metal structure is Very practical. Therefore, a triple technical task must be addressed, including: (controlling the intermediate structure of the material during ultrasonic shock to maintain the integrity of the surface being treated; (b) restoring the degraded material The intermediate structure; and (c) directly affect the structural state and characteristics of the metal during the ultrasonic shock on the surface to be treated. This technical task requires supersonic The seismic conditions must be formed at the following three times: (a) when the oscillating system is close to the surface being treated; (b) if additional corrosion is required, it is formed directly during the ultrasonic shock; and (c), at (a During the process of (b), the experimental discovery of the effect of ultrasonic shock on the treated surface ends. As shown above, the ultrasonic shock process is accompanied by two oscillation modes: (a) lumped mass concentration (lumped mass) Low-frequency oscillation; and (1) supersonic frequency oscillation of a pair of resonant 7L parts, that is, the sensor/waveguide/denter of the oscillating system. The relationship between these moving graphic parts and their amplitude and velocity is calculated and displayed. In Figure 39. 71 1336730 The positive amplitude corresponds to 0S close to TS. The formula for the displacement, velocity and acceleration at any point t is x(t)=Acos〇L>t, v(t) = - A ω sincu t, a(1;) = -A 6l>2cos ω1: The maximum speed is Αω. Therefore, the maximum speeds of 〇S and 0SE are as follows:

Vos = 2Aos7rf〇s = 0.38m/sec (maximum), while V0SE = 2A〇SE7rf0SE = 5.09m/sec (maximum). It can be seen that the oscillating system moves with two frequency classifications of the oscillating speed, where the carrier ultrasonic oscillating speed leads the oscillating system to a level close to at least ten of the response oscillating speed of the treated surface. Thus, the method of the present invention comprises the following two main conditions: (a) The ultrasonic oscillating velocity substantially exceeds the velocity of the oscillating system, and approaches the surface to be treated prior to impact (in particular, as shown, at a frequency of 27 kHz) 30 micron ultrasonic oscillating amplitude, and 200 Hz rebound frequency and 〇. 3mm rebound frequency, at least 丨〇 times); and (b) at the moment corresponding to the time interval, in the oscillating system oscillating mode Rapid change (more correctly, the number of oscillating cycles of a particular energy drive pulse, including the compensation transient process), which is sufficient to achieve a specific reduction, compensate for the sum of the approach speed and the ultrasonic oscillating speed, at the beginning of the impact The intermediate structure can be protected against unfavorable damage, and the structure and characteristics of the material to be treated can be directly affected by the surface to be treated during the impact. The conditions for forming the impact control in the stage acting on the intermediate structure of the material (i.e., the 'impact phase) are shown in Figs. 4a to 4〇c. More specifically, Fig. 40a shows "previous", in which the oscillating speed &amp; vector of 0S and 0SE has - direction ' and the combined speed Vr of 〇SE is the maximum. 72 1336730 When the 0SE contacts the TS, the maximum shock pulse Pimp is transmitted there. Fig. 40b shows "flexible contact" in which the vector of the oscillation speed of 0S and 0SE is opposite, and the resultant velocity Vr is zero at the moment of contact with the TS. More specifically, at the moment of contact, the ultrasonic component of the shock pulse is zero. Figure 40c shows the "lag/flexible shock" in which the vector of the oscillation speed of 0S and 0SE is reversed. The synthesis speed of 0SE (in the contact area) is the minimum value. The shock pulse is the minimum value. Therefore, the change in the ultrasonic oscillating speed at the end of the oscillating system will produce some initial conditions in the phase matched with 0SE to control the force pulse of the impact point: from the "hard" to increase the oscillating speed, to the oscillating The "flexible contact or impact" of the equal speed or ultrasonic oscillating speed when the ultrasonic frequency exceeds the approach speed of the oscillating system. In accordance with the present invention, a vector diagram of these states of the oscillating system is shown in FIG. The pattern in Figure 41 clearly reflects the flexible impact formation mechanism of the first contact point between the oscillating system and the surface being treated. The overlap of this mechanism on the oscillogram of the actual impact is shown in Figure 42. In the case of a flexible contact, the combined value of the ultrasonic oscillation speed of the 0S and the tool is zero at the start of the impact. In the case of a flexible shock, the resultant ultrasonic oscillating velocity of the 0S and the tool is negative at the start of the impact. In the case of a hard impact, the combined ultrasonic vibration speed of the 0S and the tool is maximum at the start of the impact. Figure 43 shows a conventional area of the UIT of the solder joint before the trench of the UIT (x10) is formed. Figures 44 and 45 show the types of intermediate structural defects under random impact conditions after ΙΠΤ, where Figure 44 shows the edge of the trench caused by local over-strengthening under random impact conditions during the UIT (x40) 73 1336730 4 Intermediate defect; while Figure 45 shows the intermediate defect in the center of the groove caused by local over-strengthening under random impact conditions during ϋΙΤ(χ160). Fig. 46 shows the intermediate structural defects after the conventional reinforcement hammering (i.e., the surface intermediate defect after the hammer hammer (χ16〇)). Fig. 47 shows the state of the intermediate structure (i.e., the groove intermediate structure) after the implementation of the UIT (xl60) according to the method of the present invention. Starting from Fig. 47, the ultrasonic shock parameters are controlled by the above method to form the surface and intermediate structure of the surface to be treated, without damage which may cause degradation of the degradation effect when the solder joint is operated. Moreover, at a depth of at least 15 dragons, dense plastic deformation regions can be seen, and a complete physical barrier is created to counter the geometric stress concentration region under long working loads, and these effects will be described in detail. After a flexible contact or a flexible ultrasonic shock, the task of forming a strengthening layer can be achieved by a method of forming part of the method of the invention, and in the surface layer and material, waves involving ultrasonic stress (for a particular material) The maximum value of the excitation task, which is the ultrasonically deformed region (with the best intermediate structure) caused by the maximum (in terms of the strength of the surface to be treated) the flexible ultrasonic shock of the power. Caused. During the processing of the subsurface layer, the control parameters of the high power control ultrasonic shock can be defined by this task. As mentioned above, the flexible phase of the ultrasonic shock must protect the treated surface from damage to the intermediate structure and produce plastic deformation in the saturated region for optimal continuation of the UIT process with minimal scattering loss on the surface, and Therefore: (4) The effective ultrasonic percussion of the dent of the shock system will be separated from the surface and excited with the surface of the ultrasonic wave stress wave of the two 74 1336730 and (b), these stress waves are combined to modify the treated surface. The protective properties to inhibit the onset or propagation of the degradation of material properties. Figures 48 to 51 show the results of changing the plastic deformation of the material to be treated under the surface of the different laws of ultrasonic shock amplitude change after the start of the ultrasonic shock. In particular, the integrated oscilloscope graph shows the relationship between the plastic deformation of the residual surface and the changing conditions of the vibration of the lms long ultrasonic shock after the flexible phase. All results are provided and the actual free drop distribution of the amplitudes within the actual value range shown in Figure 48 is compared. _48 also shows the same dependence of the amplitude and the actually used amplitude μ m, which are evenly distributed over time. In particular, Figure 48 shows the independent and specific uniform (time) distribution of 3()_ amplitude. Figure 49 shows the clear distribution of the ultrasonic amplitude on a raised parabola. The ® 5Q shows that the ultrasonic amplitude is on the parabolic line of the concave <definitely distributed. Figure 51 shows the clear increase in amplitude from _ according to the linear law. _, the above-mentioned integrated oscilloscope graphical analysis of the ultrasonic shock (after its flexible phase <), showing the plastic deformation in the task of squeaking the material to suppress metal degradation or its occurrence conditions During each defined impact situation, it can be controlled within a wide range of parks. The physical order of the ultrasonic shock effects on the metal structure is first bound by a specific task. Some general steps including the order from the initial conditions of the material to the conditions initiated by the method of the invention include the following: ^ (1) The surface material is deformed at a rate sufficient to fill the inter-die defect voids, in a flexible impact phase During the induced plastic deformation, 'maintaining the qualitative integrity and intermediate structure of the surface material 75 1336730; (2) closing the structural defect boundary under the influence of the force occurring during the plastic deformation of the surface material during the flexibility and strong phase of the ultrasonic impact; (3) Starting the defect boundary to close the surface by the effect of the elastic residual stress caused by the plastic deformation of the material to be processed by the normalized ultrasonic shock including the flexibility and the strong phase; (4) caused by the impact at the repetition rate Under the influence of the force pulse, the boundary of the defect is closed; (5) Under the influence of the ultrasonic impact, the boundary of the dying defect closes the table T, where the vector sum of the vibration velocities is the mass and distribution of the oscillating system. The relationship between the moving speed of the mass, the force generated by the synthetic shock velocity f and the ultrasonic shock In the phase determined by the pulse, the period of the ultrasonic wave at the end of the system is reduced to the seismic system, with a dent (with a dent); (6) during the action of the shock pulse and the ultrasonic wave, at the boundary of the defect The position of the defect is caused by the friction caused by the displacement, and the boundary of the defect is activated to close the surface; (7) The defect of the ultrasonic stress wave in the ultrasonic wave 1 and the closed boundary during the power pulse caused by the ultrasonic shock Boundary closing surface; ringing start (8) During the pulse action, in the temperature rise zone caused by the plastic SC shape and friction at the boundary between the structural defect and the debris, the defect boundary is activated to close the surface, by the material properties and action The phase determined by the determined control method recurs at the repetition rate of the ultrasonic shock; (9) Under the influence of static pressure, force pulse, friction, heating and ultrasonic oscillation 76 1336730 'ultrasonic self-diffusion and closed boundary Destroy; (1 〇) start the phase of the alloy phase, such as the Shi Xi Shen Temple in the alloy, as the method according to the invention controls the ultrasonic rush (11) In the stage of flexible ultrasonic contact and accompanying impact, the unstable phase (aluminum-like copper) is fixed to resist sediment in the solid solution and prevent degradation from developing; (12) Initiating the reverse self-diffusion of the precipitate in the solid solution (similar to copper in the aluminum alloy), which weakens the structural bond and creates a hidden structure under the influence of the external force acting as the core of the subsequent metal degradation. The main cause of stress concentration; in this case, during and after the flexible phase, reverse self-diffusion is the way to restore the loss strength and ductility of the alloy during normalized ultrasonic shock; (13) According to the control method of the present invention, For example, since the potential concentration of the internal stress at the degree of the nanostructure is reduced (4), the density is decreased, and during the increase period of the resistance, the phase shift is initiated due to the normalized ultrasonic shock during and after the start of the flexibility; ((4) Under the influence of ultrasonic shock, start the material structure to control itself, :,,, the flexible phase of the sound wave impact and the ultrasonic shock The normalization of the parameters is based on the structure of the surface to be treated and the material to be treated, and the specific disadvantages of rotation, f, _, recrystallization, flow, sliding, lodging, and aging are the same. Task, ^ the degree of nanostructure, microscopic and macroscopic structural debris of the material being processed; (15) starting the re-scoring, homogenizing and arranging 77 11336730 columns of the metal structure at a microscopic level as a normalized ultrasonic wave The way to increase the resistance to degradation under impact, where 'the flexible phase is controlled as defined by this task, and, afterwards, the ultrasonic shock parameters are normalized; (16) in the tissue flexible phase and defined by this task Under the influence of the process induced by the normalization of the ultrasonic shock parameters, start the non-crystallization - as the final optimization of the surface metal structure at the nanometer level; (17) Using the method of controlling the flexibility and strong phase of the ultrasonic shock To counter the degenerative build-up of metals under initial conditions; to prevent and suppress degradation in the material of the object during or after prolonged work; (18) Use the flexibility and strong phase of random ultrasonic shock to counteract the degradation of the material at the initial conditions. According to the experimental or professional data obtained by any of the above methods, prevent and suppress degradation in the material during or after long periods of work. Technical task, the solution involves controlling the flexible phase of the ultrasonic shock and the parameters of the impact itself, in the synchronism and phase (in_phase) ultrasonic oscillations in the sound series "vibration system / dent / treated surface", according to The structural sensitivity of the material being processed can be set at the output of the ultrasonic seismic system, setting the control and matching the different requirements for the approach speed and the oscillating speed. The only criterion for specifying an effective engineering solution for a task is to obtain the desired technical effect of degradation suppression with minimal energy consumption. This situation alone determines the required degree of control over the speed of action on the material before and during the ultrasonic shock. The method of the present invention is capable of protecting a metal against degradation and suppressing degradation by ultrasonic shock, including providing impact energy, determined according to a task capable of affecting at least 78 1336730 - characteristics and state of the material, and predetermined according to the dynamic strength of the material At the timing of the drive pulse, the amplitude of the ultrasonic oscillation of the ultrasonic cover system is determined in advance while the oscillation system approaches the surface to be treated. In order to achieve this, the method provides the maximum, minimum and compensation values of the composite result of the velocity vector at the beginning of the impact by setting the above-mentioned adjustable parameters of the ultrasonic shock to a range. According to the material structure under the surface to be treated and according to the requirements of the seismic system and the surface to be treated, until the end of the ultrasonic shock, during the ultrasonic shock after the seismic system contacting the treated surface, set And change the amplitude of the oscillation. The amplitude and phase of the ultrasonic oscillation are set so that the shock velocity and energy correspond to the following conditions during the approach of the shock before the oscillation system contacts the surface to be treated. These conditions can maintain the material in the surface layer. The intermediate structural integrity and the plastic deformation of the treated surface and the super-saturation heart' is sufficient to transfer the ultrasonic stress wave into the material to be treated, so that the sound loss is maintained within a range, which is clear from The extent of subsequent plastic deformation is extended to the extent determined by the Q factor of the material. The method of the present invention further comprises: maintaining a dynamic strength retention of the surface material in relation to the allowable rate of deformation thereof, and setting a degree to control the speed of the shock in the phase of the Zhensheng system approaching the surface to be treated, thereby providing material avoidance The elementality of the element and the intermediate structure of the surface layer; according to the sensitivity of the material being processed to the effect of the ultrasonic shock of k-degree, the ultrasonic wave cover intensity distribution is set during the period of the super f wave | Obtain the degree of oscillation at 79 1336730 and the distribution of ultrasonic oscillation intensity.

In the method of the present invention, the surface material is deformed at a rate sufficient to fill the voids between the grains while maintaining the integrity of the surface material and its intermediate structure during plastic deformation caused by the flexible phase of the impact. The structural defect boundary is closed under the force occurring during the plastic deformation of the surface material caused by the flexibility and strong phase action of the ultrasonic shock. On the treated surface

At least the characteristics and/or (4) of the structure and material under the surface; and, according to the experimental data or special n technology defined by this task, initially determine the elastic residual stress caused by the plastic deformation of the controlled material, start the defect The border closes the surface. It is also possible to initiate a defect boundary to close the surface under the influence of a force pulse caused by the impact at a predetermined repetition rate. The start of the defect boundary closing surface, during the ultrasonic oscillation of the shock system in one phase, the vector total cooperation system of the oscillating speed of the oscillating system and the moving mass of the oscillating system can be reduced to the oscillating system end. This phase is set by controlling the combined shock velocity and the force shock caused by the ultrasonic shock. Under the influence of friction, the defect boundary is turned off to close the surface. These frictional forces are caused by the boundary displacement of the defect during the action of the shock pulse and the ultrasonic wave. The initiation of the closed surface of the defect boundary is accompanied by ultrasonic oscillations and waves acting through the closed boundary under the action of a force pulse caused by the super-chopper impact. In the method of the present invention, the defect edge closure is also initiated in a temperature rising region which is caused by plastic deformation and friction at the boundary between the structural defect and the debris during the pulse action, in a phase The recurrence of the repetition rate of the ultrasonic shock within the system corresponds to the task of the material 80 81336730. Under the influence of the static pressure of the seismic system, the force pulse, the friction at the boundary, the heating, the ultrasonic vibration, and the ultrasonic stress wave, the ultrasonic self-diffusion and the elimination of the closed boundary occur. These are formed and controlled by this task. Set by the defined flexibility and strong phase conditions of the ultrasonic impact. In a preferred embodiment of the invention, the precipitate of the alloy phase, including the niobium precipitate in the aluminum alloy, provides increased material strength obtained by controlling ultrasonic shock. The unstable phase, similar to copper in aluminum alloys, is fixed at the stage of flexible ultrasonic contact and impact to counteract deposits in the solid solution and prevent degradation. In order to suppress degradation or to comply with metal degradation, the reverse self-diffusion of unfavorable precipitates in solid solution (similar to copper in aluminum alloys), where this unfavorable precipitate causes structural bond weakening, The concealed structural stress concentration caused by the external force is generated, and the subsequent metal degradation is induced, which is obtained by immediately normalizing the ultrasonic pulse intensity after the flexible phase, and is accompanied by the loss strength and ductility of the recovery alloy. Preferably, the phase shift initiation occurs because the ultrasonic pulse is normalized after the flexibility of the predetermined variation of the ultrasonic pulse density over time begins. Preferably, this initiation is accompanied by an increase in fatigue resistance, which is caused by the redistribution and reduction of the distribution density of the potential concentration of internal stress due to the degree of nanostructure. In a preferred embodiment of the invention, the self-control of the material structure in rotation, bending, pairing, recrystallization, flow, sliding, lodging and aging, 81 1336730 疋 by metal structure, microstructure And the fragmentation redness of the macroscopic structure during the normalized flexible phase of the ultrasonic shock and the subsequent strong phase. At the microscopic level, the re-segmentation, homogenization and arrangement of the material structure, as a way to increase the resistance to degradation, occurs during the period of flexibility and subsequent strong phase, under the influence of ultrasonic shock, wherein these parameters are normalized. As defined by this task. The initiation of amorphization occurs as the final normalization of the surface material structure to the nanometer level

This is due to the process caused by ultrasonic shock during the flexibility and subsequent phase. These parameters are normalized according to experimental or professional data, as defined by the task, to allow rapid local heating and cooling of the metal in the plastically deformed region of the metal. The flexibility and strong phase that controls the ultrasonic shock 'protects the material against degraded build-up under initial conditions' and prevents and suppresses degradation within the structural material during or after long periods of operation.

Both of these - in the preferred embodiment - (1) the aluminum alloy is protected against corrosion stripping; and/or (2) the characteristics of the aluminum alloy that has been damaged by spalling, the condition is restored and/or repaired. As described below, the effects of the method of the present invention over conventional methods of combating degradation have been described, and the use of super-functional (four) sound (four) hits of flexible phase 'provide-series degradation suppression engineering solutions and techniques to affect the surface The intermediate structure controls the ultrasonic shock parameters after the flexible phase of the characteristics of the material being processed and the conditions under the shadow surface. The following examples show the type of degradation, the degraded science, the road, the P servant aa r 4 · the degraded material is degraded, and the method of applying and converting this method according to the present invention to slap the treated surface and the treated material And inhibit degradation. One of them degenerates into mechanical fatigue. The signs of mechanical fatigue include fatigue. The fatigue process of the I-slot includes the accumulation of the elastic distortion of the lattice of the order m of τ, the increase in the density of the discharge, and the subsequent occurrence of submicro-cracks in the volume of the metal, in which the mass of the individual blocks During the sliding, a critical difference densit density is obtained; and 'finally, the micro-cracks grow into giant cracks. When this slave shape occurs, the “cracked crack” occurs along one of the most densely grown micro-cracks. Mechanical fatigue most commonly occurs in bridges, tunnels, railways, transportation load-bearing structures, and lifting equipment' aircraft and transportation (stress-concentrated areas of welded joints under load). The method of the present invention can produce a characteristic of a damaged material that compensates for a protective barrier and restores high-power flexible ultrasonic shock, and has an adaptive switching time proportional modulation of a driving pulse synchronized with the same power flexible ultrasonic shock ( 〇/QTRM). In order to implement such a drive pulse switching time proportional control, pulse width and amplitude modulation are used, and when the frequency of the synchronized ultrasonic shock increases, a small pause is required (that is, insufficient for the mutual pre-shock suppression). The length of the 5 Ge people's excessive process is not enough to independently recover the earthquake Lu's then? Burst this point. In this way, the following results can be achieved: Control the plastic deformation density distribution in time and space during each ultrasonic shock; control the surface parameters, the stress deformation state and the existing or possible in the ratio of the intermediate structure to the crystal structure The depth of penetration in the damaged area; and under the influence of external conditions (heating, load, environment), the phase is stabilized, and the structure and characteristics are homogeneous in the unstable region. Another type of degradation is corrosion fatigue. The signs of corrosion fatigue include fatigue cracks that propagate from the surface. Fatigue cracking accelerated by fatigue mechanisms is achieved by 83

The next situation arises: absorption of surface active substances; generation of chair-in effects by micro-cracks; and diffusion of hydrogen, resulting in embrittlement of metals. Most of the corrosion fatigue occurs in bridges, pipelines, tunnels, seaports, and equipment used in the chemical industry (load welding points subjected to environmental attack and stress concentration areas). The present invention is capable of resisting adsorption&apos; and prevents the adsorptive contents from being exposed to structural debris; increased mobility, loss of bond between adsorbent content and surface active material and adsorbent surface&apos; and damage to material or its structure In the region; and the optimization of roughness and residual stress in the surface, intermediate structure and surface layer, and surface material resistance to adsorption (increased material density in the surface layer). Another type of degradation is thermal and thermal mechanical fatigue. The signs of thermal and thermal mechanical fatigue include fatigue cracks. In the process of fatigue failure, the parts are periodically deformed due to low cycle or high cycle temperature effects and mechanical fluctuation stresses caused by them. When this occurs, heating can be caused by the inherent basic processes of energy acquisition, depletion, and accompanying energy during mechanical operation. Thermal and thermal mechanical fatigue occurs mostly in thermal and nuclear power plants, metallurgical plants (pots, furnaces), motor and rail transportation, and machine operations (parts of brake devices). The present invention provides increased resistance to initial conditions and thermal and thermomechanical damage during operation; maintaining and restoring material properties in accordance with a compensation barrier that produces distributed residual stress; and relieving stress in areas of cumulative thermal and thermomechanical damage Deformation gradient; filling the intergranular space in the region of the structural defect by the grain material, as well as the ultrasonic diffusion at the grain boundary, and optimizing the friction paired surface as a time to reduce the braking time Loss with heat energy. 84 Another type of degradation is chemical corrosion. Signs of chemical corrosion include: uniform KJ Pa with fine rot, plague, cracks and rot. Chemical rot (4) principles include metal environmental chemical interactions (gas or liquid), the formation of new chemical compounds on the surface to reduce material strength, and the formation of stresses and regions. The negative effects of chemical corrosion occur most frequently in chemical industry, nuclear energy engineering, pipeline transportation (oil tanks, pipelines, reactors), aircraft, marine, railway and motor transportation (case, shell armor). This φ invents the original surface to be affected and restores the material properties; modifies the intermediate structure and the crystal structure to make the surface material amorphous, according to the oscillation during the psui period in the sensing state/denter/surface system The formulation of the function of amplitude, the compensation barrier that generates residual stress in the surface material; the pulse and ultrasonic diffusion on the grain boundary in the structural failure region caused by corrosion in the crystal; and the plastic deformation of the material, the grain size is uniform The increase in properties fills the space between the grains by the grain material, and the pulsed ultrasonic waves on the grain boundaries diffuse. • Another type of degradation is electrochemical corrosion. Signs of electrochemical corrosion include: localized (depression) and extensive surface corrosion damage associated with metal decomposition. The mechanism of electrochemical exchange between metal and environment includes: anodizing a metal atom ionization, and forming ions dissolved in the solution and unfilled electrons in the metal, and electrons are transferred from the anode reaction zone to the cathode reaction zone. Where the cathode reaction zone is capable of producing a cathode treatment in terms of thermodynamics and mechanics; application of an oxidant/depolarizer to the cathode region (reaction of metal ions with electrolysis (tetra)); cathodic treatment - absorption by a depolarizer Excessive electrons, and, in the cathode region, the thermodynamic conditions for recovery treatment are provided by pin 85 1336730 for the depolarizer; and the decomposition and disturbance of surface geometric homogeneity, the weakening of structural bonds, in this region Reduced material strength. Electrochemical corrosion most commonly occurs in seaports (shell armor, thrusters), chemical industries (oil tanks: reactors), pipelines, subsurface and subsurface routes. According to the present invention, the method for suppressing the negative effects of the electrochemical rot (4) includes: under the initial condition of the material, generating an electrochemical corrosion compensation barrier and restoring its characteristics; optimizing the microscopic and macroscopic geometry of the surface, and the surface material is micro. The homogeneity of the crystal structure, the nanocrystals and amorphization of the surface material as a means of suppressing the anode treatment; the plastic deformation of the surface, the region where the compressive stress is generated, and the increase of the material density to prevent the localization of the electrochemical corrosion of the surface defects And, in the case of an optimal surface intermediate structure, the above surface conditions are formed using a PSUI mechanism. Another type of degradation is hot corrosion. Signs of hot corrosion include: material decomposition and heat generation and scale formation. The physical principles of hot corrosion include chemical interactions between high temperature priming metals and the environment. Hot corrosion occurs most often in thermal and nuclear power plants, in metallurgical plants (boilers, furnaces), and in chemical plants (reactors). The invention can generate a chemical corrosion compensation barrier under the initial condition of the material, and restore its characteristics by using the PSUI mechanism to optimize the quality, and apply a protective heat-resistant coating to increase the surface alloy depth, and if the surface material If the characteristics need to be repaired, these operations can be repeated on a scale layer as needed. Another degradation is radiation corrosion. Signs of radiation corrosion include: corrosion pits and cracks. In the kinetics of the corrosion process, the mechanisms of radiation emission include: radiolysis, which is caused by irradiation on water, and accelerated cathodic treatment due to ionization of 86 1336730 water; and destructive effects, including elasticity Interacts with the radiant particles on the hot metal surface, resulting in defects in the metal surface layer and oxide film. These defects promote anode treatment and have the most significant effect on the rate of corrosion. The negative effects of radiation corrosion occur most often in nuclear engineering, military equipment, and space systems. The invention affects the surface to be treated and the material to be treated, can generate radiation corrosion compensation protection barrier under the affected material &lt; initial condition, and restores its characteristics by using the psui mechanism; optimizes quality and applies Protective heat and radiation resistant coatings increase surface alloy depth; in terms of roughness, intermediate structure, microscopic grain structure and material amorphization, surface conditions are optimized; and a favorable compressive stress field is produced, And increase the surface material density. Repeating these operations on the damaged layer restores the radiation resistance of the surface material to the extent of the affected original material.

Another type of degradation is corrosion cracking. Signs of corrosion cracking include corrosion cracks. The mechanism of corrosion cracking includes: solution cations adsorbed on the movable row and other defects, which reduce the surface energy and promote the collapse of the atomic bond of the metal; due to the adsorption in the micro-cracks on the metal surface Crack accumulation occurs due to the intrusion of the surface active material. The rate of high crack growth in this case is caused by the accelerated anodic decomposition of the metal at the bottom of the crack, wherein the state of stress deformation is generally caused by the concentration of tensile stress. Corrosion cracking occurs most often in chemical, salt, nuclear, and pipeline transportation (oil tank 'pipeline' pressurization equipment, reactors). The method for resisting corrosion cracking of the present invention can generate a compensation barrier against the formation of corrosion cracks under the initial conditions of the material, and restore its characteristics using the PSUI 87 1336730 mechanism; optimize the quality, adhere or increase the deer The depth of the alloy applied to the protective coating on the surface that may be or is actually damaged, and the initiation of favorable compressive stresses within the surface to reinforce or improve to a predetermined depth 'under optimal or defined conditions of the intermediate structure; The structure and the resulting stress-deformation state of the material structure make the solution cations unable to adsorb on the mobile row and other defects, wherein these defects can reduce the surface amount and weaken the atomic bonding; optimize the surface intermediate structure. And preventing crack build-up, which is caused by the squeezing action of the adsorbed surface active material in the micro-cracks on the metal surface; on the surface having the best intermediate structure, a rubbing stress field is generated; Both the magnitude and depth are sufficient to resist the high cracks caused by the accelerated anodic decomposition of the metal at the bottom of the crack. Propagation, in which the state of stress deformation is generally determined by the concentration of tensile stress. Another type of degradation is hydrogen embrittlement. Signs of hydrogen embrittlement include a reduction in strength characteristics and cracking cracks. Hydrogen embrittlement mechanisms include: atomic hydrogen permeates into voids, pores and other lattice defects; hydrogen is converted into a molecular gas that produces high pressure; atomic hydrogen is adsorbed on the surface of the part, and chemical compounds are formed with metals and impurities. Impurities reduce surface energy and metal chipping resistance. Hydrogen embrittlement occurs most often in metallurgical work, as well as in engineering, salt, pipelines (welding structures, galvanizing plants), petrochemical plants (reactors), and aircraft (shell). The method for resisting hydrogen embrittlement of the present invention can strengthen the surface alloy quality, the adhesion strength and the density of the galvanized coating by using the PSUI mechanism; generate a compressive stress field on the surface and have an optimal intermediate structure, the magnitude and depth thereof. It is sufficient to resist the reduction of strength characteristics and the formation of fracture cracks, which may be caused by the penetration of atomic hydrogen into voids, pores and other lattice defects 88 1336730; hydrogen is converted into a molecular gas that produces high pressure between the sections; The adsorption of atomic hydrogen on the surface of the material, as well as the formation of chemical compounds of metals and impurities, can reduce surface energy and metal chipping resistance. Another type of degradation is liquid metal embrittlement. Signs of liquid metal embrittlement include reductions in strength characteristics and cracking cracks. The physical principles of liquid metal embrittlement include: adsorption of molten metal into the pre-destructive zone of solid metal; and reduction of surface energy and metal fracture resistance in damaged areas. Liquid metal embrittlement occurs most often in metallurgical plants (galvanizing the method of the present invention to prevent or "treat" liquid metal embrittlement, using PSUI to produce an optimal intermediate structure and compressive stress field on the surface, the magnitude and Depth is sufficient to prevent · decrease in strength characteristics 'formation of fracture cracks, adsorption of molten metal into the pre-destructive zone of solid metal, and reduction of surface energy and metal fracture resistance. Another degradation is erosion. Signs of erosion include surface fluctuations The physical principles of erosion include: the separation of the particles from the affected body surface due to the contact of the body with moving liquids, the gaseous environment or the invading females, while the particles are invaded by the solid particles and the affected surface. Invasion # most commonly occurs in pipeline transportation (pipes, pressurized equipment), aircraft industry (full wheel), marine transportation (propellers), rockets and missiles (case). 2 According to the invention, the material is inhibited or restored. The method of surface is simple: enough to produce the best density on the surface, (four) degrees, intermediate structure and compressive stress field, the amount Both the depth and the depth are sufficient to resist the separation of the solid particles from the surface of the body. This separation is caused by the contact movement of the body (4), the gas environment or the invading particles, and the particles are caused by the solid particles on the surface of the shadow. 1336730 Collision leads to intrusion. Another type of degradation is latent change. The signs of latent changes include the formation of micro-cracks and pores (micro-voids) at the grain boundaries and the formation of sub-structures. The mechanisms of latent changes include: sliding (difference pattern); Distortion; combination of sliding planes; formation of flakes; rotation and relative movement of grains; rotation and relative movement of mosaic blocks; diversification, diffusion plasticity; recrystallization mechanism; and combination of microscopic and macroscopic degrees of defects and structural damage. The most common occurrences occur in thermal power embedding and nuclear energy waste, the petrochemical industry, and aircraft (structures, reactor bodies, and high temperature operating; still wheel blades). According to the present invention, to prevent and "treat" #你的Method, using PSUI to obtain the best density, intermediate structural conditions, and package size of the grain above and below the surface, as well as compressing the giant stress The micro-stress field, its magnitude and depth are sufficient to prevent the following results: micro-cracks and holes (micro-voids), sliding (according to the difference pattern), distortion, sliding plane bending, formation on grain boundaries and substructures Thin surface, rotation and relative movement of crystal grains, rotation and relative movement of mosaic block, multi-angle, diffusion plasticity, recrystallization, and combination of microscopic and macroscopic defects and structural damage. Another degradation is microstructural degradation. Microstructure The signs of degradation include a reduction in the strength characteristics of the material. The mechanism of microstructural degradation includes the adsorption of molecules from the environment by microscopic surface length 2 (Rebinder effect) and immediate stabilization of unfavorable metal phases in a deformed body. To convert the unstable phase at the cost without significant changes (aging) within the microstructure. Microstructural degradation most commonly occurs in salty, refining furnaces (10) structures, pipelines, seaports, and aircraft (ontologies, Case layer). According to the present invention, the method for treating the microstructure degradation with 90 1336730 is based on the use of p-measurement to produce the optimum density and intermediate structure of the material on the surface of the material; the plastic deformation and compressive stress field on the surface can be normalized. The magnitude and depth are sufficient to prevent a decrease in the strength characteristics of the material due to degradation of the microstructure, which may include adsorption of molecules from the environment caused by the micro-surface growth (Rebinder effect) in the deformed body; And/or the immediate stabilization of unfavorable metal phase conditions 'at the cost of converting unstable phases without significant changes (aging) within the microstructure. Another type of degradation is radiation embrittlement. Signs of radiation embrittlement include fragmentation and cracking, with a sudden increase in the intensity of the fall. The physical principle of bell embrittlement includes a neutron flux that can move atoms or generate moving streams within a metal lattice based on the neutron energy transferred to the metal atoms, thus resulting in a volume with high vacancy concentration. , surrounded by a region surrounded by void atoms with increased density. Radiation embrittlement occurs most often in nuclear energy engineering (reactors), Tai 2 systems, and military equipment (missile body shells). According to the present invention, the method for preventing or "treating" radiation embrittlement is to use psui to obtain the optimum density and intermediate structure of the material to be processed through the plastic deformation and compressive stress field above and below the surface, and the magnitude and Depth is sufficient to prevent the above formation 'in the case of a sudden increase in the drop strength of the fracture crack, which is moved or moved by atoms in the metal lattice according to the neutron energy transferred to the metal atom (under the neutron flux) The resulting degradation, and then, forms a high concentration of vacancies that surround the periphery by enlarging the density of the void atoms. Another degradation is spalling. The signs of spalling include surface corrosion of the metal 91 1336730 彔J falls and stress concentration and strength loss are formed. The physical principles of spalling include the synergy between rot and argon embrittlement. Peeling occurs most often in aircraft. The method for preventing or suppressing ongoing corrosion spalling according to the present invention is based on the use of PSUI's degree and time parameters corresponding to experimentally obtained requirements to obtain an optimum density of the material to be processed, and the intermediate structure is guaranteed The temperability 'and' conditions for the formation and normalization of local point heating, and the heat rejection from the plastic deformation zone, the plastic deformation itself, and the compressive stress field above and below the surface being treated, Both the magnitude and the depth are sufficient to: prevent surface corrosion of the metal from peeling off, form stress concentration and loss strength, or 'recover metal properties in these damaged areas caused by the synergistic effect of corrosion and hydrogen embrittlement; prevent formation of components The formation of an unstable phase of precipitation leads to a reduction in the structural bond and strength of, for example, copper; at the boundary of the structural debris, self-diffusion is initiated, and corrosion cracking at the grain boundaries is eliminated; and macroscopic and microscopic defects on the structure are eliminated. , for example, holes or other kinds of grain breaks within the closed boundary, and start The diffusion process is provided; the reverse diffusion of the precipitate is provided, and the stable phase is restored; the precipitate of the alloying element is produced, and the concentrated density and strength of the material are increased in this region; in the concentrated region, the compensation of the mechanical stress of the structure is ensured, Distribution or relaxation, which is caused by precipitates from unstable phases of solid solution; 92 1336730 Forms an ultrafine grain structure, which is amorphous, increases the strength of the material, and on this basis Corrosion resistance. The specific engineering solutions described above can be converted to some special application examples of the metal degradation inhibition method of the invention. Hereinafter, the technical effects produced by the action of the method of the present invention using ultrasonic wave impact on different materials will be described in detail. The experimental results of this effect, the conditions thereof, and the effects obtained are also described in detail below. More specifically, hereinafter, the effect of ultrasonic shock on suppressing degradation in metal according to the method of the present invention will be described in detail. Therefore, in cast iron, the material effect obtained is that the life of the automobile brake drum and the brake disc made of cast iron is prolonged, and the results are shown in Figs. 52 to 53. Figure 52 shows the microhardness distribution, while Figure 53 shows the residual stress distribution. Preferably, the υιτ condition for obtaining the effect of this material is as follows: f-27 kHz; A_3 〇 &quot;m; pressure 21 kg; dent 6_35x25 mm, R5.5nnn; diameter 419 dragon; speed - 190 RPM;丨: Feeding—〇8mm/min; Action 2: Feeding a 0.4mm/min. This material effect can be achieved by introducing a high degree of compressive stress, an increase in the microhardness of the surface layer, and protection of the intermediate structure against damage caused by work and process. According to the present invention, another material used in the cast iron by UIT is an increased corrosion strength, and in particular, the water column iron ansi/awwa C151/A21.51-96 is made of ferroniobium of the VCh45-5 type. The results are shown in Figures 54 to 56. More specifically, Fig. 54 shows the structure of an unprocessed sample at 1 〇〇 / im ice, and Fig. 55 shows the structure of a UIT processed sample at 1 〇〇 m depth, and Fig. 56 shows the treatment by UIT The comparison of the sample and the sample JL that has not been treated by 93 1336730 UIT in tap water. The best UIT conditions for this material effect are as follows: f_44kHz A-18/if pressure 5kg; dent 5x25mm, R5 with; diameter - 23〇; speed -16RPM; feed - 〇.25mm / min. This material effect is obtained by the following method, by densely normalizing the plastic deformation of the surface layer structure Modifications to create areas of compressive stress; and to suppress surface defects that can cause damage to intermediate structures during operation. The material effect obtained in steel is the increased fatigue resistance of welded samples in Weld〇x 42〇 steel. The results are shown in In Fig. 57, preferably, the UIT conditions for obtaining the effect of this material are as follows: f-27 kHz; p- reach 9 GGW, A-30/iin · 'pressure-5 kg; ultrasonic impact duration: 1.2-3 msec This material effect It is obtained by the introduction of a high degree of compressive stress in the stress concentration region, a reduction in stress concentration, a supersonic plastic deformation, and a structural modification of the material to be processed. Ultrasonic oscillation has been established experimentally. A preferred relationship between conditions, pressure, and dent size, which can protect the intermediate structure against damage and operational damage during operation, and to prepare a surface by using PSUI. Another material effect obtained in the material is the increased fatigue resistance of the welded specimen in the Weld0x 700 steel. The results are shown in Fig. 58. Preferably, the UIT conditions for obtaining the effect of this material are as follows: f-27 kHz; P-reach; A-3Mm; pressure -5kg; ultrasonic shock duration. 0.8-1 · 2msec. This material effect is obtained by the introduction of high compressive stress in the stress concentration region. Stress concentration 94 1336730 minus y 'ultrasonic plastic deformation, and structural modification of the material being processed. The conditions for establishing the ultrasonic shock castle by experimental means have been established. The preferred relationship between the pressure and the indentation size is that the size of the indenter can be used to protect the middle of the damage during operation and the operational damage during the work of the pair k, and to prepare a surface by using the PSUI.

Another material effect obtained in steel is the 45Mnl7Ai3 steel in the spoon: corrosion fatigue strength. The result is shown in Fig. 59. Preferably, the Un condition for the effect of this material is as follows: f-2 application; p-up ^ 9_; A-30_'. pressure - 5 kg; duration of ultrasonic shock · · i 5_

Wc. This material effect is obtained by introducing a high degree of compressive stress into the treated surface and the material being processed, and modifying the structure. It has been experimentally established that the conditions, pressures, and dents of the ultrasonic vibrations are better, which is sufficient to ensure intermediate structures during operation (4), and the ultrasonic wave impact is used according to the method of the present invention. And deal with a surface.

The additional material effect obtained in steel is (10) increased impact strength in the bridge type steel. The result is shown in Figure 6Q, which is good. The UIT conditions for this material effect are as follows: f-alp, _w; A-3Q~pressure-5kg; ultrasonic shock duration m This material effect is obtained by the following method And obtained by the rice structure: (4), and the area where the pressing force is generated, the compressive stress is sufficient to prevent the damage of the intermediate structure, and the effect of the ultrasonic static and dynamic load on the material to be processed, Supersonic; = This task is defined by the operational force. Hand You Putian 95 1336730 Another material effect obtained in steel is the grain refining in SUJ2 and S33C high strength steel. The result is shown in Fig. 61. Preferably, the UIT conditions for obtaining the effect of this material are as follows: f-27 kHz; A-25, 30 and 33 #m; pressure 20 kg; indenter 6.35 x 25 mm; diameter 5 mm; speed 500 RPM; Ultrasonic shock duration: 1. 5-1. 6msec. This material effect is obtained by intensive ultrasonic plastic deformation of the material to be processed, arrangement of the bulk structure of the nanometer degree, and suppression of damage of the intermediate structure. Another material effect obtained in the steel is that a "white layer" is obtained in the 10Mn2VNb steel welded joint of the main pipeline and the SUJ2 high strength steel sample, and the results are shown in Figs. 62 and 63. More specifically, Fig. 62 shows the welded joint of 10Mn2VNb steel, and Fig. 63 shows the sample of SUJ2 high strength steel. Preferably, the UIT conditions for obtaining the effect of this material are as follows: For 10Mn2VNb steel: f-27 kHz; P - reach g 〇 OW; A - 30 μm; ultrasonic shock duration: 0. 8_ 12 msec . For SUJ2 steel: f-27 kHz; A-25, 30 and 33em; NI80; pressure _20 kg; dents a 6.35 x 25 mm; diameter one ~ 5 mm; speed - 500 RPM. This material effect is obtained by normalizing the ultrasonic shock at high deformation load rates, dense ultrasonic shock deformation of the surface material, and rapid heat removal from the impact area. Another material effect obtained in steel is the influence of the υπ pair on the crystallization of the weld metal of the welded carbon steel ship lOCrSiNiCu, which includes: (1) a tree shape in the untreated joint (before UIT) The structure is thicker than the treated solder joint (after UIT); (2) the grain structure, preferably having 96 1336730 finer grains 'common in UIT-treated ocean joints; (3) The dendrites in the untreated solder joints before the UIT are longer and wider in the thicker intergranular layer after υιτ. The results are shown in Figures 64 and 65. More specifically, Figure 64 shows the weld without UIT, while Figure 65 shows the weld with UIT. Preferably, the υιτ condition for obtaining the effect of this material is as follows: f — 27 kHz; Α 30 μ m; pressure 20 kg; dent 1 6.35 χ 25ππη; ultrasonic impact duration: 15_2 msec. This material effect is obtained by the following methods, the strengthening of the diffusion process, and the recrystallization of metal under the action of ultrasonic waves, sound flow, sound pressure, and holes, which are caused by the ultrasonic shock and super The oscillating system of the oscillating system is triggered by the ultrasonic oscillating dent of the carrier oscillating synchronization. Another material effect that affects the structure and state of the material is obtained by sintering the powdered steel. This effect provides enhanced mechanical properties of steel samples containing 〇4%c, 0.85% Μ〇, and remaining Fe, including: (1) a density increase of up to 4.9%, and (2) an increase in strength of up to 32?^ ϋπ before The structural state of the sintered sample after UIT is shown in the figure and the middle respectively. The conditions for obtaining the effect of this material are as follows: f-27kHz, A-28/zm; NI64; pressure-nkg; concave Tracer—6. 35x25mm; Feed: 400_/min; Transverse feed: 0 5_/stroke; static extrusion with a degree of Y5Ys; duration of ultrasonic shock: 12_2msec. This material effect is obtained by the intensive ultrasonic plastic deformation of the surface material and the activation of the diffusion process caused by the ultrasonic waves during the &amp; The material effect obtained by the UIT of the present invention in an aluminum alloy is that the fatigue limit of the sample made of the 97 6061T6 alloy is increased by 2%, and the fatigue limit of the structure equal to such a welded joint is increased by m. The results are shown in Figure 。. Preferably, the conditions for obtaining the effect of this material are as follows: f - 27 kHz; P - up to 9 _; a - up to 3 〇 _; processing speed for every 2 actions is 1, 2 Sec / c: m, ie For heavy # solder joints, each action is 〇.6sec/cm; ultrasonic shock duration: 12_&quot;(four)c. This material effect is obtained by introducing a high degree of compressive stress, reducing stress concentration, and creating physical barriers against the formation of intermediate structural defects, each of which is located at a specified plastic deformation and compressive stress corresponding to the extent of the defect. In the area. Another material effect obtained in aluminum alloys is the increased high cycle fatigue strength, especially in the aluminum alloy AA5〇83 (or A1Mg45Mn), for 8mm overlapping joints and samples with longitudinal attachments About 疋80%. The results are shown in Figures 69 to 7B. More specifically, map 69 shows the S_N curve of the 8_sample with the longitudinal attachment, while Figure 7〇 shows the S-N curve of the 8 mm sample with the overlapping joint. Preferably, the UIT conditions for obtaining this material effect are as follows: f_27 kHz; p - up to 9 〇〇 w; a up to 3 〇 vm; duration of ultrasonic shock: i.2_17 msec. This material effect is obtained by introducing a high degree of compressive stress, reducing stress concentration, and suppressing intermediate structure damage which may occur by ultrasonic recrystallization in a solid solution, and ultrasonic waves in the present invention. The initiation of ultrasonic diffusion at the grain boundaries during the impact. Another material effect obtained in the aluminum alloy is to suppress the near surface (especially the casting porosity of up to 2.5 mm), and the wheel made of alloys such as AlSi7Mg, AlSi9Mg 98 1336730 and A!Sil!Mg, The results of the car wheel are shown in Figures 7J to 72. The UIT condition of β # 可Ρ is good, and the UIT condition for obtaining the effect of this material is as follows: f— ^ . n , / Z7kHz, feed—400 jobs/min: lateral feed. 0. 5πππ/stroke ;pressure 15 g β 〇c 9ς g ' A , action〗··dentation benefit—6·35χ25πππ, R5. 5mm: action ultrasonic shock duration door.&quot;Bu 9.〇5X25,R1°mm; 曰Pi (4) duration. To defeat. This material effect is by

In the tens of thousands of styles, the intensive plastic deformation of the near-surface layer of the treated material is obtained at the boundary of the ultrasonic wave at the boundary of the defect, the closure under the impact of ultrasonic waves, the form of the hole or fracture in the material of the material, and the suppression of normalized plastic deformation. Intermediate structural defects in the region with compressive stress, corresponding to the degree of plastic deformation 'in the normalized ultrasonic shock of the present invention and its influence on the structure', in particular, the material which is deformed by ultrasonic shock , during the propagation of ultrasonic stress waves, reduced deformation resistance caused by. In addition to the increased strength of the material to be treated 7, another material effect known from the σιτ according to the present invention is that the sustained impact strength of the material to be treated is made, in particular, from A1Si7Mg, AlSi9Mg, and the like. The results of the casting wheel are shown in Figures 73 to 74. More specifically, the ® 73 shows the impact strength on the sample with the reinforced indentation, and Figure 74 shows the impact strength on the sample cut from the reinforcing wheel. The uiT and Ultrasonic Impact Processing (UIM) conditions can be used to fix the impact strength in a densely plastically deformed region caused by an impact load at the initial material height. In the region where the ultrasonic stress wave is caused by the ultrasonic shock, the impact strength is increased by 12%. Preferably, the UIT conditions for obtaining the effect of this material are as follows: f-27 kHz; feed- 4 〇〇 off/min; 99 1336730 pressure 15 kg; pin - 9. 05 x 25 mm; RO. 25 mm; Condition 1 : A-10/im; Condition 2: A-20/zm; Condition 3: A-3030; Ultrasonic Impact duration: 1. 2-1. 7 msec. Additional UIT conditions are: f __ 27 kHz, dent - 6.35 x 25 mm; R25 mm; UIT condition: action 1: A-20 # m; action 2: A-12 em; V-18 m/min; 〇. 5mm/rev ; dents a 6. 35x33mm; R25mm; action 1: pressure a 15kg and Α - 22

Mm, Action 2: Pressure 7kg and A-12 &quot;m; Ultrasonic impact duration: 1. 2-1. 7msec. Since during the UIM and UIT, structural distortion may occur under dense plastic deformation, it may lead to the prevention of the difference of the rows, and other defects are formed in the grain ratio on the material to be processed, which are according to the present invention. Defined. Among the stress concentration conditions after the UIT, the impact strength of the Charpy sample is directly related to the sample size, that is, the relationship between the deformation and the volume of the undeformed material. For ease of explanation, the Charpy test is a pendulum type single blow impact test in which a sample with a generally dent is supported at both ends as a simple beam and at the dent by a drop of the pendulum impact (dynamic The stress concentration device) is broken. The absorbed energy is measured by the wire to measure the impact strength or dent, which is calculated by raising the pendulum later (following the impact of the ruptured sample). Further, the Charpy value is directly affected by the condition of the intermediate surface of the dimple, which is controlled according to the present invention by the normalized plasticity (4) during the action of the ultrasonic shock and the ultrasonic wave induced by the present invention. The other material effect obtained by the UIT' according to the present invention in the aluminum alloy is that the (IV) content of the solid solution of the AlSUlMg alloy is the alloy content and the material strength is increased. This result is shown in Figure Μ to π 100 1336730. More specifically, Figure 75 shows an untreated sample structure, Figure 76 shows the ruthenium precipitate on the UIT-treated sample, and Figure 77 shows the micro-hardness distribution in the untreated sample and UIM sample depth, clearly Shows the sinking due to the contents of the layer in this layer; the temple, the treated surface at a depth of at least 2 mm and the micro-strength of the material being processed. Preferably, the UIT conditions for obtaining the effect of this material are as follows: f—27 kHz; V—18 m/min; feed a 0·5 mm/rev; dents a 6.35×25 mm, R25 mm; action 1: extrusion A 15kg and A-22 / / m; action 2: squeeze a 7kg and A-12 / im; ultrasonic impact duration: 1.2-1. 7msec. The UIM of the present invention can obtain this material effect by reinforcing a surface layer by a structural change therein. In this surface layer, a more solid co-solubilized structure (a + Si ) + Si) is formed by the two-phase condition of the initial structure (α + co-solvent U + Si) + Si). This process is also accompanied by the fact that the contents move into the surface under the influence of ultrasonic shock, and substantially reflect the objective ability of strengthening the A-Si alloy due to the precipitation of ruthenium in the near surface layer. According to the UIT/UIM of the present invention, another material effect obtained in the aluminum alloy is the property of the 2024-T351 alloy which restores the corrosion peeling. After the UIT of the present invention, the exfoliated sample has a 33% increase in the drop strength (19% for untreated and unpeeled materials) and a final strength increase of 24% (for untreated unpeeled materials, after UIT/UIM, Can be increased to the general strength of the material within the precise measurement range). This result is shown in Figures 78 to 79. Preferably, the UIT conditions for obtaining the effect of this material are as follows: f—36 kHz; dents 5×17 mm, R25 mm; A—18 # m; NI64; calendar force 3 kg; feed: 400 mm/min; Give: 0. 5min / stroke; ultrasonic shock duration: 1.0-1. 3msec. This material effect is obtained by the supersonic 101 wave impact diffusion at the grain boundary. The other material effect obtained by the UIT' in the aluminum alloy according to the present invention is to increase the cycle life of the sample. The 7075_T6 alloy is well formed and cut from the wing's case panel, in a slightly corroded sample with a factor of 3.2 and a severely corroded sample with a factor of 2.9. Fig. 8A shows the effect of the UIT of the present invention on the fatigue resistance of samples having different degrees of corrosion. Preferably, the UIT conditions for obtaining this material effect are as follows: f - '36 kHz; dents 5 x 7 mm, R 25 mm; A - 20 ym; NI 64; pressure - 3 kg; feed - 400 mm / min; Mm. 5mm / stroke; ultrasonic shock duration: 1.0-1. 3msec. The present invention unchanges the crack collection mechanism. Therefore, for a corroded sample without UIT, the crack starts to accumulate from intergranular cracks at the interface between the corroded region and the substrate, and the crack does not aggregate for the sample in which the UIT of the present invention is subjected to slight corrosion. This effect can be achieved by mechanically closing the grain boundaries and then spreading the ultrasonic waves in areas of intergranular corrosion damage under the influence of dense ultrasonic plastic deformation. According to the UIT of the present invention, another material effect obtained in the aluminum alloy is a more refined structure of the cold-rolled sheet of 2024-T351 alloy (average from ΐ6·52ηιπ to 8-lmn), compared to the initial state. This result is shown in Figures 81 to 82. More specifically, Fig. 81 shows the surface layer before the ruthenium treatment, and Fig. 82 shows the finer grain structure refined by the UIT. Preferably, the UIT conditions for obtaining the effect of this material are as follows: f - 36 kHz; dents - 5 x 17 mm, R 25 mm; A - 15 / zm; NI 64; pressure - 3 kg; feed: 1000 mm / min; 〇5mm/stroke; ultrasonic shock duration 102 1336730: 0.9-1. 2msec. The reason for this material effect of grain refining is as follows: due to additional deformation, a high-difference density and a paired structure are formed; a micro-f structure is formed, and the micro-structure is sub-divided into submicron grains; and, the sub-crystal The granules are further broken into equiaxed (eqUiaxecj). According to the UIT of the present invention, another material effect obtained in the alloy of the alloy (especially the cold-rolled sheet of 2024-T351 alloy) is the movement of the precipitate and the generation of a microbelt of l〇-15mn width. This is accompanied by a process in which the submicron grains are self-aligned, and the resistance of the intermediate structure to mechanical and corrosion damage of the nanoscale in the surface layer is increased. Therefore, 'the two effects that occur due to the UIT of the present invention are an increase in the microhardness in the surface layer' and an increase in the static strength of the material, and a decrease in the distribution density of the deposited material (that is, a structural stress concentration) causes fatigue. The conditions for strength improvement 'and the structural homogeneity in the surface layer increase. This effect is shown in Figures 83 to 85. More specifically, Fig. 83 shows the microhardness distribution, Fig. 84 shows the surface layer structure before the UIT process of the present invention, and Fig. 85 shows the microstrip in the UIT sample. Examination of precipitates using energy dispersive spectroscopy (EDS) indicates that these precipitates are rich in A1, Cu, Fe, Μ, and Si. However, the density of these precipitates was found to have a minimum at the surface of the UIT as well as near the surface. As a result of comparison with the as-rolled state, it is shown that the size of the precipitate after the UIT exhibits a reduced ratio, and its density shows a maximum within the band. By comparing the above observations as a whole, the potential stress concentration distribution density is generally reduced at the structural level. This can be considered as a necessary condition for increasing the ability of the material to resist the formation of fatigue damage. Preferably, the UIT conditions for obtaining the effect of this material are as follows: f - 36 kHz; pin 5 x 17 mm, R 25 mm; A - 18 / / m; NI 64; pressure - 3 kg; feed: 103 丄ΓΓΓΓ lateral feed: GW Stroke; duration of ultrasonic shock: 乂: sec. This material effect is obtained by the geometric dynamic recrystallization process, and the energy and high temperature can reach a critical level.

To the children; the temples move. In the role of Ren Fu #主# A in the 仃h shape, this effect is accompanied by the normalization of ultrasonic shock, local heat, heat removal, normalized ultrasonic distribution, etc. .

According to the UIT of the present invention, the material effect obtained in the yellow _ is an increase in the rot strength, especially the eu3 brass pusher (10) lgFe4N14)e. The results are shown in Figs. 86 to 87 +. More specifically, Fig. 86 shows that the rot (four) is bad on the untreated sample surface and Fig. 87 shows the sample surface after the UIT. The best UIT conditions for obtaining this material effect are as follows: f - 27 kHz; p - 900 W; A - up to 3 〇 _; pin - 3 x 2 〇 mm, R3 (four). This material effect is obtained by introducing a high degree of compressive stress.

Modifying the surface layer structure, the ultrasonic wave that is closed at the boundary of the structural defect such as the hole, resists damage' and suppresses the intermediate structure damage of the microscopic and macroscopic extent. Since the cracks with different natures show the final evidence of the main types of metal degradation, the specific methods of UIT effects in the dynamics of crack initiation and development include: (a) "very" smooth surface , the roughness of which, for example, does not exceed 〇., and the residual compressive stress is induced to a relatively small depth (〇7, j), wherein such a surface allows for a "long-term" delay in crack initiation, which may occur after the start Faster crack development, and suppression by the UIT technique of the present invention described above; 104 1336730 (b) Smooth surface with roughness above 0.5/zm, intact intermediate structure, and compressive stress induced to 15mm intermediate depth, which will allow for greater material resistance to crack initiation and growth after the start, to a more pronounced depth in the south compressive stress field, but not less than 〇. 1.5mm; (c) intact a smooth surface of the intermediate structure of the surface (less surface damage can reach a depth not greater than 〇〇〇3), fine grains in the subsurface layer, and compression Is induced to a greater depth of 2. 5mm, thus, resulting in greater material resistance to cracks after the start, and slowing crack growth, in the area of fine grain structure and compressive stress field; (d) complete Non-destructive surface smooth surface of the intermediate structure (less surface damage can reach no more than 〇. 〇〇 8mm depth), fine grain and amorphous structure in the near surface layer, and compressive stress is induced to the maximum of the specified material Depth (up to 4 mm), using controlled ultrasonic shock, thus resulting in greater material resistance to cracks after initiation and slowing crack growth in areas of fine grain and/or amorphous structure And continuous crack prevention in the compressive stress field, these compressive stresses can substantially resist the fall strength of the material being processed. In addition, 'the crack starts to harden, and the following effects of u I τ of the present invention can prevent the development of fatigue cracks: (a) diffusion bonding of the crack boundary; (b) the crack development zone is immersed in the residual compressive stress zone (crack) ()) Remove the cracked metal surface layer (like grinding) to the undamaged metal. The above material effects can be obtained by controlling the supersonic 105-wave impact parameters during the flexible and strong phase, and it is the main criterion for the smashing of the ultrasonic shock parameters. «Experimental or professional materials, ^. The requirements of the depth of the rape. Therefore, μη mm can be set to the ultrasonic impact parameter. Because of the prominence of controlling the deep-impact parameters of the ultrasonic shock parameters, the synthetic speed at the beginning of the special $βA impact is particularly at the 'shock amount' repetition rate, and the impact = amplitude and phase' is based on the specificity of the experimental or professional data.

= Defined 'where' these parameters are set to arbitrary values with 5% dispersion based on actual results according to specific technical requirements. b The above results demonstrate that the high technical efficiency of the ultrasonic shock technique of the present invention (developed according to this month) can suppress the occurrence of metal degradation and the degradation that occurs during the operation of the machine and structure.

The cockroaches to be known can be used to prevent or suppress the above-mentioned types or signs of degradation on the material by means of the above-mentioned engineering singularly or in combination, to provide at least one desired material effect, to achieve any desired technical effect or task. For example, corrosion-based degradation can be dealt with individually to achieve a technical effect, or, for example, in combination with thermal rupture and/or surname&apos; to achieve another technical effect. Thus, different data elements are interchangeable to achieve different results or technical effects for different tasks. Many variations may still be made to those skilled in the art within the scope of the above description. Such modifications, which fall within the capabilities of those skilled in the art, still form part of the present invention and are covered by the scope of the following claims. BRIEF DESCRIPTION OF THE DRAWINGS Figure 1 shows the effect of lifetime on the variability of the tube metal of MnSi steel (T5()) to 106 1336730 (previous technique). Figure 2 shows the relationship between the time when the crack occurred and the initial stress intensity coefficient Ki of the 17MnSi steel pipe (previous technique). The steel pipe has three samples: (1) just manufactured, (2) working pipe', and (3) emergency pipe. . Figure 3 shows the effect of work on the tendency to deform aging (prior art). Figure 4 shows the area reduction of the aged tube (prior art). Figure 5 shows the time dependence of the internal friction Q-1 of the tube metal of 17MnSi steel after 3 years of extended work (prior art). Figure 6 shows the time dependence of the internal friction q-1 of the tube metal of 17MnSi steel in emergency stock (prior art). Figure 7 shows the potential damage mechanism associated with high temperature applications of aluminum alloys (prior art). Figure 8 shows a different classification of hydrogen damage (prior art). Figure 9 shows a schematic of an electrochemical corrosion process (prior art). Figure 10 shows a schematic diagram of the formation of a dual electrochemical layer in which metal atom ions are converted into a solution (prior art). Figure 11 is a schematic view showing the formation of a double electrochemical layer of a cation which is converted from a solution to a metal surface (prior art). Figure 12 shows the integrity of the surface microhardness data obtained on the surface of the tube section (steel X65) after the emergency stock tube and 2 years of operation (prior art). Fig. 13 shows the surface crack initiation and crack growth of the original material having specular precision and having a fracture shape (shear mode growth) which clearly indicates the growth of the end face (prior art). 107 1336730 Figure 14 shows surface crack initiation and crack growth of the original material with EDM accuracy and near surface area showing multiple crack core evidence (prior art). Fig. 15 shows an end face region having a depth of about 15 延伸 and an end face region surrounded by crack-like fatigue cracking, S11q_2qq%_45. The corner crack start position of the CS0 sample (previously, Fig. 16 shows crack initiation and early crack growth with LSP 10GW/cm2 (2 actions) indicating the start of the surface crack, the fracture branch and the fracture pattern of the propagation path (previous technique) Figure 17 shows crack initiation and early crack growth (previous technique) with LSP 10GW/Cm2 (3 actions) indicating the start of surface cracks, fracture branches, and fracture patterns of the propagation path. Figure 18 shows that it can be pointed out from a typical The crack initiation of the surface crack of the projectile hammer and the double treatment of the fracture pattern of the fracture branch begin with the early crack growth (previous technique). Figures 19 and 20 show the cubic lattice of the center of the space or body (previous technique). Figures 21 and 22 show a face centered cubic lattice (prior art). Figures 23 through 25 show the major sliding crack planes in a simple cubic lattice (prior art). Figure 26 shows the microstructure of cast iron (prior art). Microstructure of annealed iron (prior art). Figures 28 to 30 show the sliding under the tension of a single crystal round sample of zinc. Prior art.) 108 1336730 Figure 31 shows the microstructure of deformed iron (prior art) Figure 32 shows the microstructure of undeformed iron (prior art) Figure 33 shows the sliding line on the unetched metallographic section of iron (previously Fig. 34 and 35 show a oscillating system in which the elastic restoring force caused by the oscillating system bounces back from a treated surface, and the ultrasonic vibration of the barrier system connected to a dent Under the influence, the ultrasonic shock is accompanied by the movement of the shock system.

Figure 36 shows the plastic deformation distribution during the ultrasonic shock of the present invention. Figure 37 shows the frequency plot of the ultrasonic shock. Figure 38 shows an arbitrary aligned random ultrasonic shock. Figure 39 shows a portion of the graph of an instantaneous motion of a oscillating system. Figures 40a through 40c show the previous, soft contact and hysteresis/flexible impact of the velocity vector of this quake system at the end of the oscillating system that is reduced to a dent handle.

Figure 41 shows a vector diagram of the velocity of the shake system of Figure 40as40c. Figure 42 shows an oscilloscope graph of an arbitrary aligned ultrasonic shock. Figure 43 shows the conventional area of the solder joint before the formation of the trench of the UIT. Figure 44 shows the intermediate defects on the edge of the trench caused by local over-strengthening under random impact conditions during UIT. Figure 45 shows the intermediate defects in the center of the trench caused by local over-strengthening under random impact conditions during UIT. 109 1336730 Figure 46 shows intermediate structural defects after conventional reinforcement hammering. Figure 47 shows the state of the interstitial structure of the trench after the UIT is implemented in accordance with the method of the present invention. Figure 48 shows the independent and well-defined uniform (time) distribution of the 30 μm amplitude. Figure 49 shows the clear distribution of the ultrasonic amplitude on a raised parabola. Figure 50 shows the clear distribution of the ultrasonic amplitude on a concave parabola. Figure 51 shows a clear increase in amplitude from the beginning according to the linear law. Figure 52 shows a graph of the microhardness distribution of cast iron. Figure 53 shows a graph of the residual stress distribution of cast iron. Figure 54 shows the corrosion strength of an iron-free structure of an untreated sample at a depth of 100/zm. Figure 55 shows the improved corrosion resistance of a UIT-treated sample at a depth of 100 μm. Figure 56 shows the results of a comparison of tests conducted in UHT-treated and untreated samples in tap water for corrosion. Figure 57 shows a graph of improved fatigue resistance for most welded steel samples, which were individually welded, after the UIT with a 5mm pin, after the iron clock, after the hammering, and by TIG After that, after TIG finishing and then implementing UIT, and using the 3mm pin to implement UIT. Figure 58 shows a graph of improved fatigue resistance of a welded sample of steel. 110 1336730 Figure 59 shows a graph of improved corrosion fatigue strength of steel. Figure 60 shows a graph of test results for improved impact fatigue strength of steel. Fig. 61 shows a re-segmentation structure of a high-strength steel having a grain reduction range. Figures 62 and 63 show the i〇Mn2VNb steel welded joints in a main pipe and the white layer in the high-strength steel SUJ2. Figures 64 and 65 show the effect of UIT on metal crystallization in welded carbon shipbuilding steel. Figures 66 and 67 show the improved mechanical properties of the steel samples. Figure 68 shows a graph of the S-N curve for an 8 mm short-handle weld to show the fatigue limit of a sample made of aluminum alloy. Figure 69 shows a graph of the s-N curve of an 8 mm sample with a longitudinal attachment to show an improvement in the high cycle fatigue strength of the welds in the aluminum alloy. Figure 70 shows a graph of the S-N curve for an 8 mm sample with overlapping contacts to show an improvement in the high cycle fatigue strength of the solder joints in the chain alloy. Figure 71 and Figure 72 show the reduction in porosity to a depth of 2. 5 mm, and the life extension of the cast wheel made of the alloy. Figures 73 and 74 show the sustained impact strength in the treatment of cast wheels made of aluminum alloy. Figures 75 and 76 show the sinking in the aluminum alloy. Figure 77 shows a graph of the microhardness distribution of the precipitate of cerium in an aluminum alloy. Figures 78 and 79 show the improvement in the strength characteristics of the aluminum alloy after the corrosion peeling. 111

Claims (1)

1336730 No. 095135182 February 25, 1999 曰 修正 修正 修正 修正 修正 修正 修正 修正 修正 修正 修正 修正 、 、 、 、 、 、 、 、 、 、 、 、 、 、 、 、 、 、 、 、 、 、 、 、 、 、 、 、 、 、 、 、 、 、 、 The impact energy defined by at least one property or state of task and depending on the dynamic strength of the material, the method comprises the steps of: predetermining the timing of the drive pulse initiation during the oscillation system approaching the surface to be treated to provide the integrity of the surface intermediate structure The phase and amplitude of the ultrasonic oscillation at the end of a supersonic seismic system are in a range including the maximum value, the minimum value, and the compensation value of the resultant velocity vector at the beginning of the impact; and after the ultrasonic shock contacts the surface Set the oscillating amplitude during the ultrasonic shock to change the oscillating amplitude to affect the material structure under the surface to be treated, and according to the requirements of the oscillating system to bounce back from the surface to be treated until the end of the ultrasonic shock, where the oscillating system and surface During the approach period, set the ultrasonic oscillation before the oscillation system contacts the surface. Amplitude and phase, resulting in At the beginning of the contact, the velocity and energy of the impact correspond to the condition that the intermediate structural integrity of the material in the surface layer can be maintained, so that the surface to be treated is deformed to a degree that does not exceed its saturation value, but is sufficient to Within the material, the sound loss is maintained within a range that is sufficient for the specified subsequent plastic deformation, but does not exceed the range determined by the material q factor. A method of using ultrasonic waves to counter metal degradation and suppress degradation, which is an impact that can affect the at least-property or state of the material as defined by the task and according to the dynamic strength of the material, the method comprises the following steps: 113 2. 1336730 + month 曰 repair (more) is replacing the page in the shock 4 system close to the desired period by the time of the construction of the integrity of the 'predetermined drive pulse, the phase and amplitude of the ultrasonic shock at the end of a supersonic shock system Within a range, the range includes the maximum value, the minimum value, and the compensation value of the resultant velocity vector at the beginning of the impact; and after the ultrasonic shock contacts the surface, 'set and change the oscillation amplitude during the ultrasonic shock to affect the surface to be treated Bottom material knot And according to the requirement that the oscillating system bounces back from the surface to be treated until the end of the ultrasonic shock; in the stage of the system approaching the surface after the earthquake, according to the dynamic strength of the surface material related to the allowable rate of deformation, the setting is To control the degree of oscillating speed, thereby providing the integrity of the intermediate structure between the material and the surface layer; and setting the ultrasonic oscillation during the ultrasonic shock according to the sensitivity of the treated material corresponding to the ultrasonic shock effect exceeding the specified state. Strong The degree distribution is sufficient to obtain at least one characteristic of the material structure and the material under the surface; wherein the degree of control of the oscillation speed and the distribution of the ultrasonic oscillation intensity is initially determined based on experimental data or the expertise defined by the task. 3_ As in the method of claim 1, the further step includes: in the stage of the arrival of the seismic system close to the surface, according to the dynamic strength retention of the surface material related to the allowable rate of deformation, setting the degree of control of the oscillation speed Thereby providing a complete t 114 .99. 2. 0 5 property of the intermediate structure of the material and the surface layer; and a 1 2; during the ultrasonic shock, according to the ultrasonic impact of the material being processed corresponding to the excessive to the finger state Sensitivity, setting the ultrasonic oscillating strength knives, which is sufficient to obtain at least the characteristics of the material structure and the material under the surface; wherein 'the degree of control of the oscillating velocity and the intensity distribution of the ultrasonic oscillating intensity, It is initially determined based on experimental data or the expertise defined by the task. The method of any one of claims 1 to 3, wherein the rate and energy of deformation of the negative surface of the material during the deformation of the 2 and the flexible impact phase predetermined by the task are sufficient to fill the crystal There is a gap between the two particles, and the integrity of the material surface and its intermediate structure is maintained. The method of any one of claims 1 to 3, wherein the boundary of the defect is closed under the influence of force, and the force is super What happens during the plastic deformation of the material surface caused by the soft and strong phase of the chopping wave. The method of any one of claims 1 to 3, wherein the defect boundary is closed to the surface under the influence of elastic residual stress caused by plastic deformation of the surface of the material. The method of any one of claims 1 to 3, wherein the defect boundary is closed by the effect of a force pulse caused by an impact having a predetermined repetition rate. • The method of any one of claims 1 to 3, wherein during the ultrasonic oscillation of the ultrasonic oscillation system at the end of the phase, 5 1336730 '9a 2. .0 5 , Λ '4 repair (more) positive: the dynamic defect boundary closure surface is accompanied by the vector sum of the oscillating velocity of the moving mass of the oscillating system oscillating system, reduced to the seismic system end, which corresponds to the phase in which the synthetic seismic velocity is obtained. And a pulse of force caused by the ultrasonic shock, wherein the synthetic shock S speed and the power pulse are pre-determined by the task. 9. The method of any one of the preceding claims, wherein, during the action of the shock pulse and the ultrasonic wave, the boundary of the defect boundary is activated under the influence of the friction force induced by the displacement of the defect boundary . For example, in the method of claim ii to 3, wherein during the action of the power pulse caused by the ultrasonic shock, the start of the defect boundary closing surface is accompanied by ultrasonic shock a and passing through the closed boundary. The role of waves. U. The method of any one of claims 1 to 3, wherein in the control phase, the repetition rate of the ultrasonic shock recurs and the material characteristic is matched with the pulse specified by the task, and the temperature is raised. In the region, the dynamic defect boundary closes the surface, and the temperature rise is caused by plastic deformation and friction at the boundary between the structural defect and the debris. 12. The method of any one of claims 1 to 3, wherein the closing of the static pressure of the oscillating system, the force pulse, the friction of the boundary, the heating, and the ultrasonic wave stress wave of the ultrasonic wave occur. Ultrasonic waves on the boundary spread and destroy themselves. The method of any one of claims 1 to 3, wherein the precipitation of the alloy phase, including the cerium precipitate in the aluminum alloy, provides an added material strength 'and due to the control of ultrasonic shock And was opened [ 116 1336730 | 9τ; ------· ί moving. Year of the month. Japanese repair (more) Zhengzhi 14. If you apply for patent scope! The method of any of the three items, wherein the indefinite phase 'includes copper in the alloy, in the ultrasonic contact and impact of the 13⁄4 & in the fixed ' to resist the solid matter in the solid solution and prevent Degeneration occurs. 15. The method of any one of the preceding claims, wherein the reverse self-diffusion of the sinking matter in the solid solution, including the copper of φ in the chain alloy, causes the structural bond to weaken, resulting in The concentrated structural stress concentration caused by external force and the subsequent metal degradation caused by the normalization of the ultrasonic shock after the flexible phase of the ultrasonic shock' and the loss of strength and ductility of the alloy . 16. The method according to any one of the preceding claims, wherein, since the ultrasonic shock is being fucked after the start of the flexible phase, the start of the phase shift occurs, which is accompanied by fatigue resistance. • The increase in density is due to the reduced density of the potential concentration of internal stresses at the nanostructure level. Such as the scope of patent application! The method of any one of the three, wherein the self-control of the metal structure in the rotation, bending, pairing, recrystallization, flow, sliding, undulation, and aging is a nanostructure, a microstructure, and a giant view of the metal The fragmentation level of the structure is initiated due to the control of the formation of the flexible phase and the subsequent normalization of the ultrasonic shock parameters. 18. The method of any one of claims 1 to 3, wherein, 117 1336730 ##f日修(更&gt; is replacing f I with a microscopic degree of riding a knot as an increase in degradation resistance In this way, the starting system is under the influence of ultrasonic shock, due to the soft phase of the ultrasonic shock defined by the mission. 20. And the subsequent normal phase parameters are normalized. Such as the scope of patent application! The method of any one of the three, wherein the amorphization is initiated to be the final optimization of the surface material structure of the nanoscale, which is too long due to the dynamic model defined by the task. As a result, the dynamic model is used to control the soft phase and normalize the parameters of the ultrasonic shock. Such as the scope of patent application! The method of any of the three items, wherein controlling the soft and strong phase of the ultrasonic shock is used to protect the metal against degradation build-up under initial conditions, and to prevent and inhibit structural damage during or after prolonged operation The material is degraded. The method of any one of claims 4 to 3, wherein the aluminum alloy is protected against corrosion and spalling, and/or, restoring and/or repairing other characteristics of the aluminum alloy that have been damaged by spalling . The method of any one of claims 1 to 3, wherein at least one technical effect is obtained, comprising: synchronizing with a high power soft ultrasonic shock by a high power soft ultrasonic shock (PSUI) The drive pulse is adapted to the switching time proportional modulation (0/0TRM)' to generate-compensate the protection barrier and restore the characteristics of the damaged material, wherein in order to implement such control of the drive pulse switching time ratio, the pulse width is used Amplitude modulation, which is caused by the increase in the frequency of the synchronized ultrasonic shock - the length of the pause or _excessive process is 118 to start, and the pause is not sufficient for independent predetermined shock suppression between the two, and The excessive process is not sufficient for independent recovery of the oscillation, thereby achieving: controlling the plastic deformation intensity distribution in time and space during each ultrasonic shock; controlling the surface parameters by the ratio of the intermediate structure to the microcrystalline structure, the material Stress-induced shape and depth to penetrate into existing or potentially damaged areas, and/or external strips in heating, load and/or environment Under the influence of the unstable region, the stable phase, homogeneous structure, and a metal characteristic. The method of any one of claims 1 to 3, wherein at least one technical effect is obtained, comprising: combating adsorption and preventing the adsorptive content from contacting structural debris; increasing mobility, and adsorbing the contents and surface The bond loss of the active material to the adsorbent surface, the damaged area of the material, or the material structure; and/or the roughness of the surface to be treated, the intermediate structure, and the surface, and the surface layer by increasing the density of the material in the surface layer The residual stress and the resistance of the surface material to adsorption are optimized. The method of any one of claims 1 to 3, wherein at least one technical effect is obtained, comprising: adding resistance to thermal and thermomechanical damage at initial conditions and during operation; maintaining and restoring material properties, Relieves stress in areas of cumulative thermal and thermomechanical damage based on the compensation barrier that produces distributed residual stress and 1336730 The method of optimizing the frictional coupling surface is optimized by at least a deformation gradient of 0 scoops, 2, 5, and 超, and ultrasonic diffusion at grain boundaries. In order to reduce the time and heat loss of the brakes 25. For example, the scope of patent application! To the method of any of the three items, and obtain at least one technical effect, including: ^ Protecting the affected original surface and restoring the material properties; Modifying the intermediate and microcrystalline structure, the surface material is amorphous, resulting in Compensation barrier for residual compensating stress in the surface material, which is based on the formulation of varying oscillating amplitudes in the “sensor/denter/surface” system during high power flexible ultrasonic shock; In the region where the structural damage is caused, the pulse and ultrasonic diffusion at the grain boundary; and/or the plastic deformation of the material increases the grain size, the space between the grains is really full, the space between the grains, or the crystal The method of any one of claims 1 to 3, wherein at least one of the technical effects is obtained, comprising: generating an electrochemical corrosion compensation barrier in an initial condition of the material, And restore at least one of its characteristics; strengthen the microscopic and giant geometry of the surface, the homogeneity of the microcrystalline structure on the surface of the material, and the nanocrystallization of the surface of the material Value, as a way to prevent anode treatment; 120 1336730 » ------- 丨 _.· 期〇 _ _) front;:; 表面 a surface deformation deformation, the area that produces compressive stress: and increase the law The localization of electrochemical rosting that prevents surface defects by alpha; and/or the use of a power flexible ultrasonic shock mechanism to form enhanced surface conditions and surface intermediate structures. 27. The method of any one of the preceding claims, wherein at least one of the technical effects is obtained, comprising: generating a chemical smear compensation barrier in the initial condition of the material by using a high-power flexible ultrasonic shock mechanism And restore at least one of its characteristics to enhance the quality and increase the depth of the surface alloy, and 'if necessary and need to repair the material properties, the protective coating on the scale layer should be (4) protective heat-resistant coating and repeat these operations. 28. The method of any one of claims 1-3, wherein at least one of the technical effects is obtained, comprising: using a high power flexible ultrasonic shock mechanism to generate radiation corrosion in an initial condition of the affected material Compensating for the barrier and restoring at least one of its characteristics; thereby applying a protective heat and radiation resistant coating to enhance the quality and increase the depth of the surface alloy; ϊ 粗 这, intermediate structure, micro-grain structure and amorphous material In terms of chemistry, 'enhance surface conditions; and generate favorable compressive stress fields, and increase the surface material density. Repeat these operations on a damaged layer to restore the surface material to the sum of the affected initial materials. Radiation resistance. 29. The method of any one of claims 1 to 3, wherein 121 1336730 obtains at least one technical effect, comprising: The monthly repair &lt;more&quot; is replaced by the use of a high power flexible ultrasonic shock (PSUI) mechanism to create a compensation barrier against the formation of corrosion cracks in the initial condition of the material, and to restore at least one of its characteristics; Thereby enhancing the quality, adhesion or increasing the depth of the alloy applied to the protective coating on the surface that may be or actually damaged, guiding the favorable compressive stress into the surface of the material, in order to strengthen under the strengthening or specific conditions of the intermediate structure Or modified to a predetermined depth; Modifying the material structure and generating the stress-deformation state of the material structure can prevent the solution cations from being adsorbed on the moving row and other structural defects. These defects can reduce the surface energy and weaken the atomic bonds; due to adsorption on the surface of the material The rubbing action of the surface active material in the microcracks to strengthen the surface intermediate structure and prevent crack buildup; and/or On the treated surface with the strengthened intermediate structure, a compressive stress field is generated which is both large in magnitude and depth to resist the high crack propagation rate caused by accelerated anodic decomposition of the metal at the bottom of the crack, where ' The state of stress deformation is generally determined by the concentration of tensile stress. 30. The method of any one of claims 1 to 3, wherein at least one technical effect is obtained, comprising: using a high power flexible ultrasonic shock (PSljI) mechanism; thereby enhancing surface alloy quality, adhesion strength And the density of the galvanized coating; and/or on the treated surface having the reinforced intermediate structure, a compressive strain of 122 1336730 is generated, the magnitude and depth of which are sufficient to counteract the reduction in strength characteristics and the cracking of the crack. Formed, the cracks are caused by at least one of the following: atomic hydrogen permeates into voids, pores or other lattice defects; hydrogen is converted into a molecular gas capable of generating high inter-fragment pressure; and/or atomic nitrogen is adsorbed to the part On the surface with internal defects, these internal defects are formed with chemical compounds of metals and impurities, which can reduce the surface energy of the material and the resistance to chipping. The method of any one of claims 1 to 3, wherein at least one technical effect is obtained, comprising: using a high power flexible ultrasonic shock to generate a strengthened intermediate structure and a compressive stress field on the surface, the amount Both the value and the depth are sufficient to counteract the reduction in strength characteristics, the formation of fracture cracks, the penetration of molten metal into the pre-destructive zone of the solid metal, the reduction of surface energy, and the resistance to metal fracture. The method of any one of the U.S. patents, wherein Obtaining at least one technical effect, including: using high-power flexible ultrasonic shock to produce enhanced penetration, roughness, intermediate structure and compressive stress field on the surface, the magnitude of which is deeper &quot; = against solid particles and material structure separation This separation is due to the movement of the liquid, the gaseous environment or the invading solid particles, which are caused by the impact of the particles on the surface of the (4). The method of any one of clauses 1 to 3, wherein, at least one of the technical effects comprises: using a back-powered flexible ultrasonic shock to generate a dense density on the surface 123 d. I; month 9 repair (more)瞀 瞀 Platinum;; y intermediate structural conditions and grain package size r; force "microscopic stress field, its magnitude and depth contrast: micro-cracks and pores (microvoids) formation on grain boundaries and substructures , sliding, pairing, bending of the sliding plane, forming a sheet of 'rotation and relative movement of the grains, = rotation and relative movement of the gram block, polyhedification, diffusion plasticity, recrystallization ' and/or to microscopic and giant The degree of combination of defects and structural damage. Team = the method of applying for any of the items in items 1 to 3 of the Patent Park, in which at least one technical effect is obtained, including: Using high-power flexible ultrasonic shock, the material's reinforced density and intermediate structure are produced on the surface of the material, as well as plastic deformation and compression on the surface. The magnitude and depth are sufficient to prevent degradation due to microstructure. The resulting reduction in the strength properties of the material, including degradation of the molecules from the environment by the development of the microsurface into a deformed body, and/or metal phase conditions in time; at the expense of unstable phase conversion, but 35. The method of any one of claims 1 to 3, wherein at least one of the technical effects is obtained, comprising: using a high power flexible ultrasonic shock through the surface The normalization of the upper and lower plastic deformation and the compressive stress field, and the obtained material and the intermediate structure of the material to be treated, the magnitude and depth of which are sufficient to prevent the sudden increase of the fracture strength of the fracture crack, which is transferred according to the neutron to The energy of a metal atom is caused by the movement of atoms or moving streams under the influence of the pre-current in the metal lattice. And, after a high concentration to prevent more air 1241336730) v j being replaced missing missing black lines along the periphery of the subject to the original sub-region having the void density increase surrounded. The method of any one of claims 1 to 3, wherein at least one technical effect is obtained, comprising: The use of high-power flexible ultrasonic shock, the degree and time parameters correspond to the requirements found in the experiment, to obtain the strengthening density of the material to be processed, and the guaranteed density of the intermediate structure, and for the formation and normalization of local point heating. The conditions, as well as the rate of heat rejection from the plastic deformation zone, the plastic deformation itself, and the compressive stress field above and below the surface to be treated, are both of magnitude and depth sufficient to prevent metal surface rot and form stress concentration and Loss of strength, or recovery of metal properties in these damaged areas, caused by the synergistic effect of corrosion and hydrogen embrittlement; preventing the formation of unstable phases that can cause precipitation of materials, resulting in a reduction in structural bond and material strength, And intergranular corrosion; - Elimination of microscopic and macroscopic defects in the structure, including porosity or other intergranular fractures that close the boundary and initiate the self-diffusion process; initiate self-diffusion of the boundary on the structural debris and eliminate the boundaries at the grain boundaries Corrosion cracking; - Provides reverse diffusion of precipitates and restores stable phase; - Provides deposits of alloying elements to increase concentrated density and strength of treated materials; - Ensures compensation and redistribution of structural mechanical stresses in concentrated areas Or slowing down 'this is caused by the precipitation of 125 1336730 from the unstable phase of the solid solution, and / or - forming ultra-fine grain structure and corrosion resistance. Amorphous, increase material strength to For example, in the method of claim 1 to 3, wherein at least one result is obtained, including: ίInto a large degree of compressive stress, the increase in the micro-hardness of the surface layer, and the damage caused by the work and process of the protection of the rider and the brake disc (4). 38. The method of any of claims 1-3, wherein the obtaining at least one result comprises: modifying the surface structural layer by intensive normalized plastic deformation to create a region of compressive stress, and/ Or suppress surface defects that may cause damage to the intermediate structure during operation to increase the corrosion strength in the scale tube. For example, please ask for the scope of patents! The method of any of the three, wherein the obtaining at least one result comprises: In the stress concentration region, a large amount of shrinkage stress is introduced, the concentration of the force is reduced, the ultrasonic deformation of the ultrasonic wave, and the structural modification of the material to be processed: the conditions of the ultrasonic shock, the pressure and the size of the dent are ensured to protect the middle. The structure is more resistant to damage caused by the process during the work, and the surface is prepared by high-power flexible ultrasonic shock to increase the fatigue resistance of the welded steel. For example, the method of any one of the claims of the invention, wherein the obtaining of at least one result comprises: introducing a large amount of compressive stress to the surface to be treated and the material to be treated [S 126 1336730 . V pa: 2··: 丨o fei repair (more) just replace w:; and modify its structure, in which the super-sonic, -pressure-other-pass-size device can ensure the protection of the intermediate structure during work, and ensure the use of inverse super Sonic shock treatment - surface to enhance the corrosion fatigue strength of steel. 1. The method of claiming any one of the patent scopes i to 3, wherein obtaining at least one result 'includes: 乂 nanometer ranks a block structure, and the zone 1 compressive stress generating compressive stress is sufficient Static and (iv) During the action of the load on the material being treated, the intermediate structure is prevented from being damaged to enhance the impact strength of the steel. These loads are caused by the normalized ultrasonic shock and operating force defined by the task. 42. If you apply for a patent scope! The method of any one of the preceding claims, wherein at least one result is obtained, comprising: dense ultrasonic plastic deformation of the material being processed', arranging the intermediate structure in a nanometer scale, and/or inhibiting damage to the intermediate structure of the steel material. 43. If the method of any one of the patents is applied to any one of the three items, to obtain at least one result, including: under the influence of the normalized ultrasonic super shock of a large deformation rate, the surface material Dense ultrasonic plastic deformation, local warm-up in the phase transition region, and/or rapid heat removal from an impact region, thereby obtaining a white layer in the steel. 4. The method of any one of the patent scopes 至 至3, to obtain at least one result, including: under the action of ultrasonic waves, sound flow, sound pressure and cavitation, strengthen 1336730 [" In addition, the 扩散 Γ Γ 扩散 扩散 扩散 扩散 扩散 扩散 扩散 扩散 扩散 扩散 扩散 扩散 扩散 扩散 扩散 扩散 扩散 扩散 扩散 扩散 扩散 扩散 扩散 扩散 扩散 扩散 扩散 扩散 扩散 扩散 扩散 扩散 扩散 扩散 扩散 扩散 扩散The method of any one of claims 1 to 3, wherein at least one result is obtained, comprising: dense ultrasonic plastic deformation of the surface material, and/or caused by ultrasonic waves during ultrasonic shock The initiation of the diffusion process, thereby enhancing the mechanical properties of the steel.曰 46. The method of claim 1, wherein the obtaining of at least one result includes: introducing a large degree of compressive stress, reducing stress concentration and/or creating a physical barrier to counteract the designation The plastic deformation and intermediate structural defects in the region corresponding to the compressive stress of the degree of defect are formed to thereby strengthen the fatigue limit of the alloy. 47. The method of claim 9, wherein obtaining at least one result comprises: introducing a large degree of compressive stress, reducing stress concentration, and/or borrowing ultrasonic waves from the solid aa Crystallization and initiation of ultrasonic diffusion at the 4 boundary during ultrasonic shock, while inhibiting possible intermediate structural damage ' thereby enhancing the high cycle fatigue strength of the alloy. 48. The method of any of the items of U3 of the patent scope, wherein at least one result is obtained, including: s under the effect of normalizing ultrasonic shock and the influence of ultrasonic shock on the material, Intensive plastic deformation of the treated material, the back surface layer, 128 1336730 ΐ' / ''Τ'?7·------- j hand repair (more) is replacing * Γ border (4) sound pure, money t^ 曰下下' and the occurrence of holes or fractures in the material and/or suppression of the plastic deformation of the lining and the intermediate structure defects in the area corresponding to the degree of pure deformation, wherein the effects In particular, the ultrasonic wave is caused by the reduced deformation resistance in the material which is deformed by the ultrasonic shock, thereby suppressing the porosity to a predetermined degree of ice and prolonging the life of the aluminum alloy. The method of any one of the claims, wherein the obtaining at least one result comprises: maintaining or increasing the impact strength in the metal (including the steel and the alloy) due to the plastic deformation of the super-printed wave, Among them, the impact strength can be reduced under the influence of the conventional plastic deformation, which results in the reduction of the plasticity of the material, due to the plasticity of the recording, the difference in the structure, or other structural defects. The method of any one of claims 4 to 3, wherein at least one result is obtained, comprising: a structural change due to predetermined control of the ultrasonic shock parameter during ultrasonic surge processing a reinforced surface layer, in particular steel; the conversion of the two-phase condition of the initial structure in the surface layer, in particular in an aluminium alloy, and the formation of a more solid eutectic structure; and/or the movement of the alloy contents onto the treated surface, in particular It is the ruthenium content in the aluminum alloy, thereby strengthening the affected surface. The method of claim 4, wherein at least one result is obtained, comprising: I 129 1336730; ·*~——··~·--, ;99, 2, 05^ The supersonic age of the grain boundary is more complicated.) The miscellaneous/skin impact is applied to restore the characteristics of the aluminum alloy. The method of claim 4, wherein the method of obtaining at least one of the results includes: providing 曰0 refining on the surface, particularly in the aluminum alloy and increasing its strength, = point is due to formation The increased difference «degrees and because of the extra deformation, the '° structure' forms a microstrip structure, and the microstrip structure is subdivided into Liu submicron grains. Or the sub-grain advances and destroys the scale axis and so on. 53. For example, the method of applying for the patent scope 1st $^1 to 3 of the items, wherein at least one result is obtained, including: 曰 providing the geometric dynamics of the grain with nanometer and microscopic grades 'Where the impact energy and the local heating temperature reach a level that is important relative to the material's favorable structural conditions, and can move in the microstrip in the micro-belt (4). This is due to normalization. This ultrasonic shock, local heating, heat removal, ultrasonic distribution strip The article 'and the normalization of the plastic deformation of the metal, etc., are accompanied by an increase in the resistance of the metal strength and the characteristic deterioration. A method of claiming any one of the scopes of claim 5, obtaining at least one result, comprising: ” introducing a large degree of compressive stress, tampering with the surface layer structure, and supersonic diffusion that is closed at the boundary of the structural defect containing the hole, Corresponding to damage, and suppressing the intermediate structure damage of the microscopic and macroscopic degree, thereby strengthening the corrosion fatigue strength of the brass. Only 55. For example, any one of the first and third items of the patent application garden; 130 1336730 Whole fruit, including repair (more) In the soft force: under the condition of structural integrity, the control of the ultrasonic shock: strong phase, can be changed in the rot-containing book including the alloy of the alloy = crack assembly mechanism 'where the crack in the middle grain corrosion damage (4) And development, by closing and then eliminating its boundaries: stop: the point is caused by dense plastic deformation and subsequent ultrasonic expansion &amp; Resistance. 56. The method of arranging the term "part" of the patent scope, the dynamics of the assembly and development of cracks of different nature, which can be used as the main last evidence of the main types of metal degradation' by controlling the softness of ultrasonic shock With the strong phase 'spot 彡 _ dynamics, the dragon is suppressed and this degradation is achieved, and the following effects are obtained: - a smooth surface having a roughness of not more than 〇5em, and the residual compressive stress is induced to a depth of about 0.7, wherein such a surface will delay the initiation of the crack; a smooth surface having a roughness of 0.5 々m or more, intact The intermediate structure, as well as the compressive stress is induced to a depth of approximately 15 mm, which will cause the crack initiation and growth of the material after the start to resist, and is allowed to a predetermined depth in a large number of compressive stress fields, but not less than Approximately 1. 5 mm; a smooth surface having a complete lossless surface intermediate structure, wherein less surface damage can reach a depth of no more than about 0. 3 〇 3 mm, fine grains in the subsurface layer, and compressive stress are induced to A depth of about 2.5 mm 131 1336730, thus, resulting in higher material resistance and slowing crack growth in the region of fine grain structure and compressive stress field, for crack initiation after initiation; and/or - a smooth surface with a complete lossless surface intermediate structure, wherein less surface damage can reach depths of no more than about 0.08 mm, fine grain and amorphous structures in the near surface layer, and use of controlled super The sonic impact causes the compressive stress to be induced to a maximum depth of 40 mm within the specified material, thus resulting in a higher material resistance to crack initiation in the region of fine grain and/or amorphous structure. Sexuality, slowing crack growth, and continuing crack prevention in the compressive stress field, these compressive stresses can roughly resist the lodging strength of the material being processed; wherein the initial crack produces hardening, and the developing fatigue crack is prevented by: Diffusion bonding of crack boundaries; immersion of crack development zone to residual compressive stress zone and preservation of cracks; The ruptured metal surface layer is removed from the undamaged metal by the strong phase of the ultrasonic impact. The method of any one of claims 1 to 3, wherein the at least one ultrasonic shock parameter is controlled, and the combined velocity 'shock energy, repetition rate, and impact time' impact amplitude at the start of the impact is The phase 'this parameter' is defined according to the specific task of the predetermined data, wherein at least one parameter is set to an arbitrary value with a dispersion of 5% according to predetermined technical requirements and a predetermined result to be generated. 132