氢气环境下2205双相不锈钢的氢致开裂研究

为了研究氢气环境下双相不锈钢疲劳裂纹萌生和扩展的影响规律,建立氢气环境下双相不锈钢疲劳应变组织演化—氢致开裂之间的关联机制,在5 MPa氢气和5 MPa氮气2种环境中对2205双相不锈钢试样进行了慢应变速率拉伸和疲劳裂纹扩展速率试验。结果表明：在氢气环境下,2205双相不锈钢在慢应变速率拉伸过程中的氢脆敏感性不高,而在疲劳过程中氢脆现象显著,5 MPa氢气环境下2205双相不锈钢的疲劳裂纹扩展速率比氮气环境中的快18倍;氢气能够促进2205双向不锈钢疲劳裂纹尖端周围组织的局部塑性变形,并进一步导致氢致开裂。在氢气环境下2205双相不锈钢疲劳变形过程中,不同的相结构其氢致开裂机理也不同,铁素体相容易形成河流状花样断口形貌(解理断口),而奥氏体相断口形貌多呈现平行的滑移带特征,奥氏体相在铁素体相的解理开裂过程中对裂纹具有阻碍作用。     

Z6CNT18-10奥氏体不锈钢扩散管在蒸汽疏水环境中的疲劳开裂特征

采用金相显微镜、扫描电镜、X射线衍射仪等对Z6CNT18-10奥氏体不锈钢扩散管在蒸汽疏水环境下的疲劳断口特征进行了研究。结果表明:与常见的疲劳裂纹常起源于外壁不同,在蒸汽疏水环境下的奥氏体不锈钢扩散管的疲劳裂纹起源于内壁,裂纹源处存在明显的氧化现象;裂纹附近的显微组织中存在一定量的驻留滑移带,疲劳条带间距很窄,几乎不存在瞬断区,属于高周疲劳。     

空气和腐蚀环境下双相不锈钢SAF2507的疲劳性能

对超级双相不锈钢SAF2507分别在空气和3.5%NaCl溶液中进行旋转弯曲疲劳实验,研究两种介质下SAF2507不锈钢的疲劳性能。结果表明:宏观上,双相不锈钢SAF2507在3.5%NaCl腐蚀环境中的疲劳强度较空气中的下降幅度小,为空气下的90%。但微观上,空气中疲劳断口表现为韧性断裂,在铁素体和奥氏体相上呈现大量疲劳辉纹;腐蚀环境下,奥氏体为韧性断裂,而铁素体呈现解理断裂模式。两相上疲劳辉纹的宽度和间距随着晶粒位向及二次裂纹的开裂而不同。在奥氏体-铁素体双相不锈钢的疲劳断口中,不能根据疲劳辉纹的间距进行相的鉴别。     

特种设备用双相不锈钢抗点蚀性能研究

点蚀是不锈钢最有害的腐蚀形态之一,点蚀往往是应力腐蚀裂纹和腐蚀疲劳裂纹的起始部位。点蚀是一种腐蚀集中于表面的很小范围内,并深入到金属内部的腐蚀形态,一般形状为小孔状,其危害性比均匀腐蚀严重得多,会引起爆炸、火灾等事故。双相不锈钢兼有铁素体和奥氏体的特性,它将铁素体良好的强度、硬度和奥氏体优良的塑性和韧性结合起来,并具有优良的耐点蚀性能,无论是在力学性能上还是在耐腐蚀性上,双相不锈钢都明显优于铁素体不锈钢和奥氏体不锈钢,可以在点蚀环境中的特种设备上广泛使用。     

金属工程材料腐蚀疲劳行为研究进展

合金钢、不锈钢等金属工程材料在服役过程中受到交变荷载以及腐蚀性介质的共同作用,使工程结构发生腐蚀疲劳,造成金属工程材料的承载能力降低和服役寿命缩短。因此,揭示载荷-环境体系下材料的腐蚀疲劳开裂规律对工程结构的前期设计及使用寿命预测都有深远意义。金属工程材料腐蚀疲劳失效的机制包括裂纹萌生和扩展两部分。目前的研究主要集中于裂纹扩展寿命,对裂纹萌生的研究较少。裂纹萌生机制仍存在争议,主要的观点有点蚀加速裂纹形成理论、滑移带优先溶解理论、保护膜破裂理论和吸附理论等。目前,关于腐蚀疲劳裂纹扩展机制的研究主要有阳极溶解和氢致开裂两种观点。影响腐蚀疲劳寿命的主要因素分为材料因素、力学因素及环境因素三方面。目前力学因素的研究主要集中于应力比、加载频率、加载波形等;材料因素的研究主要为显微组织及合金元素;环境因素的研究包括介质温度、浓度、含氧量、pH值及外加电位等。本文综述了金属工程材料腐蚀疲劳开裂机制及影响因素的研究现状,归纳了金属腐蚀疲劳的研究成果与不足,并在此基础上提出了下一步的研究方向及发展趋势,为相关领域的研究人员提供新思路。     

悬臂弯曲加载10CrNiMo钢的S-N曲线试验研究

采用有限元方法,计算了在悬臂弯曲加载方式下,不同载荷作用时板状光滑试样施力点处的挠度;采用成组试验法,通过载荷控制模式,进行了应力比为-1时10CrNiMo钢的S-N曲线试验,并对试样断口进行了观察和分析。结果表明:在试验载荷范围内,所设计试样施力点处的挠度变化,在试验机作动器的有效行程内,可满足S-N曲线试验,通过试验获得了两种常用置信度下10CrNiMo钢的S-N曲线;在大载荷往复作用时,表面裂纹从试样上、下两个表面萌生并扩展所形成的面积基本相当,但在小载荷循环作用下,表面裂纹通常先从试样的一个表面萌生并扩展,当裂纹扩展至一定程度时,试样另一个表面才开始萌生疲劳裂纹,并协同前一表面的裂纹共同扩展至试样断裂。产生这种现象的原因,和不同大小的载荷开动试样上下两个表面材料内部滑移系的数量、材料内部组织的不均匀性,以及裂纹在扩展过程中前缘应力状态的变化有关。     

石油钻杆材料G105在不同条件下的疲劳断裂

采用国产PQ-6型旋转弯曲疲劳试验机研究钻杆管体材料G105的弯曲疲劳性能以及H_2S腐蚀和缺口对试样弯曲疲劳性能的影响,利用金相显微镜和扫描电子显微镜对光滑试样断口、缺口试样断口以及H_2S腐蚀后试样断口进行微观形貌分析。结果表明:在光滑试样的疲劳极限载荷作用下,经过H_2S腐蚀后的光滑试样的疲劳寿命和缺口试样的疲劳寿命相当,材料的疲劳寿命都从106降低至104;缺口试样在缺口的高应力集中效应下,加快疲劳裂纹形核过程。H_2S腐蚀对钻杆疲劳性能影响的主要作用在于氢原子在材料内缺陷处聚集引起材料疲劳性能降低,缺口和H_2S腐蚀都会加快疲劳裂纹的扩展。材料疲劳断裂主要是因为试样在交变应力的作用下上产生滑移最后致使位错塞积而导致的。     

加工硬化对304不锈钢应力腐蚀裂纹裂尖力学性能的影响

压力管道中应力腐蚀开裂(SCC)是奥氏体不锈钢的主要失效形式之一,同时冷加工变形对材料的力学性能和裂纹的萌生及扩展会产生一定影响。本工作首先利用疲劳拉伸机获取304不锈钢不同冷加工硬化下的材料本构参数,同时利用有限元仿真软件ABAQUS建立了SCC裂纹裂尖宏观分析模型及子模型,研究不同加工硬化下304奥氏体不锈钢材料的SCC裂纹裂尖应力应变、J积分及裂纹扩展速率的影响。结果表明,材料在20%冷加工率变形内,随着材料加工硬化程度的增加,SCC裂纹裂尖Mises应力、J积分逐渐增大,裂纹裂尖应变(PEEQ)减小,一定程度加工硬化会促进和加速304不锈钢发生应力腐蚀开裂。     

敏化处理对Z3CN20-09M不锈钢高温水应力腐蚀的影响

为了研究敏化处理对Z3CN20-09M不锈钢高温水应力腐蚀行为的影响,使用敏化处理的Z3CN20-09M不锈钢制成U弯试样,并置于250、290及320℃的高温水中进行应力腐蚀开裂实验,采用扫描电镜观察了高温水实验后试样的氧化膜厚度以及应力腐蚀裂纹的萌生及扩展行为.结果表明:敏化处理增加了氧化膜的厚度,降低了耐蚀能力,使SCC敏感性增大;温度较高时,敏化处理的影响较大;铁素体相容易被侵蚀,大多数点蚀坑产生于铁素体中;SCC裂纹优先在点蚀坑底部和奥氏体/铁素体相界位置处形成;相界面对SCC裂纹的影响取决于SCC裂纹相对于相界面的取向,SCC裂纹扩展方向平行于相界面时裂纹易沿着相界扩展,SCC裂纹扩展垂直于相界面方向时相界面对裂纹扩展起阻碍作用.     

平面应力状态“铁素体-奥氏体-铁素体”异质接头疲劳特性

针对10Ni5Cr Mo V钢采用0Cr18Ni24Mo6N奥氏体焊条焊接形成的"铁素体-奥氏体-铁素体"异质接头,采用薄片试样疲劳试验研究了无加强高和带加强高两种情况下平面应力状态接头的疲劳行为,并建立了带加强高接头S-N疲劳曲线。结果表明,无加强高情况下疲劳裂纹在焊缝金属内启裂并扩展;带加强高情况下疲劳裂纹在焊趾处启裂、并近似垂直载荷方向在母材内扩展至断裂,寿命较无加强高情况大幅降低,且启裂寿命占疲劳总寿命的比例较高,达到70%—80%。     

Crack initiation mechanisms for low cycle fatigue of type 316Ti stainless steel in high temperature water

Low cycle fatigue (LCF) tests were performed for a type 316Ti stainless steel (SS) in high temperature water. Fatigue crack initiation behaviors in high temperature water were investigated. It was found that there existed several kinds of Ti-bearing precipitates, consisting of isolated TiN or duplex (Al, Mg)O/TiN, Mo-rich (Ti, Mo)C and Ti(N,C) in the steel. Fatigue cracks were mainly initiated at Ti-bearing precipitates, phase boundaries of austenite/α-ferrite phases and persistent slip bands (PSBs) in austenite. It is believed that synergism between the mechanical factors and electrochemical reactions played a key role in the process of fatigue crack initiation in high temperature water. Related fatigue crack initiation mechanisms for the 316Ti SS are discussed.     

Influence of bulk damage on crack initiation in low‐cycle fatigue of 316 stainless steel

To investigate the effect of bulk damage on fatigue crack initiation, crack initiations due to low‐cycle fatigue of Type 316 stainless steel were observed by electron backscatter diffraction (EBSD) and scanning electron microscopy. The EBSD observations showed that local misorientation developed inhomogeneously due to the cyclic strain, and many cracks were initiated from the slip steps and grain boundaries where the local misorientation was relatively large. The crack initiations could be categorized into two types: enhancement of the driving force by geometrical discontinuity (slip steps and notches), and reduction of material resistance against crack initiation caused by accumulated bulk damage at grain boundaries. In particular, more than half of the cracks were initiated from grain boundaries. However, in spite of the significant bulk damage, the fatigue life was extended by removing the surface cracks under strain of 1 and 2% amplitude. The stress state at the microstructural level was changed by the surface removal, and the damaged portion did not suffer further damage. It was concluded that although bulk damage surely exists, the fatigue life can be restored to that of the untested specimen by removing the surface cracks.     

MICROSTRUCTURAL AND ENVIRONMENTAL EFFECTS ON FATIGUE CRACK PROPAGATION IN DUPLEX STAINLESS STEELS

Abstract— Fatigue crack initiation and propagation in duplex stainless steels are strongly affected by microstructure in both inert and aggressive environments. Fatigue crack growth rates in wrought Zeron 100 duplex stainless steel in air were found to vary with orientation depending on the frequency of crack tip retardation at ferrite/austenite grain boundaries. Fatigue crack propagation rates in 3.5% NaCl solution and high purity water are increased by hydrogen assisted transgranular cyclic cleavage of the ferrite. The corrosion fatigue results are interpreted using a model for the cyclic cleavage mechanism.     

SHORT CRACK FATIGUE BEHAVIOUR IN A MEDIUM CARBON STEEL

The initiation stage and short crack behaviour in torsional fatigue of a 0.4% C steel was investigated by a replication technique. The fatigue cracks initiated and propagated in the ferrite phase which is located at the prior austenite grain boundaries in the form of long allotriomorphs. At this stage of crack development it is proposed that crack growth rate depends on the extent and intensity of plasticity at the tip of the crack. Crack growth per cycle is correspondingly proportional to the strength of the slip band. The ferrite-pearlite boundaries are strong barriers to crack propagation, which is manifested by a deceleration of growth and possible arrest. On raising the stress level the previously non-propagating cracks may continue to grow by branching or joining with other cracks in the ferrite phase. This process is repeated until the stress fields of one or more dominant cracks attain a critical value to sustain continued growth that leads to failure.     

CONTINUOUS SEM OBSERVATIONS OF CREEP-FATIGUE DAMAGE PROCESSES

In order to examine the relation between damage evolution and changes in microstructure, e.g. from creep cavities, surface micro-cracks and dislocation structures at high temperature, strain controlled creep-fatigue tests were performed and interrupted at several damage levels on Types 304 and 316 stainless steels. The creep-fatigue tests on Type 304 stainless steel at a low strain level were conducted in a high-temperature fatigue testing machine combined with a scanning electron microscope, and the micro-crack initiation and growth behaviour were continuously observed to clarify the damage extension mechanism. It was found that even though many cavities were initiated and grew on the internal grain boundaries of the specimens during the strain-controlled tests, the failure life was governed by the propagation of surface cracks. On the other hand, micro-cracks of about the order of one grain size were initiated mainly along grain boundaries normal to the loading axis under low stress creep-fatigue, and the crack propagation rate of the micro-cracks was slow and random due to the nature of the microstructures. The micro-cracks gradually opened in the loading direction with increasing number of cycles and coalescence contributed to growth.     

Investigation of crack initiation and propagation behavior of AISI 310 stainless steel up to very high cycle fatigue

Fatigue behavior up to very high cycles for AISI 310 stainless steel has been investigated. The fatigue crack initiated from the surface of the material. It was found that up to 10⁶ cycles, cracks initiated from the carbide precipitates at grain boundaries. However, above 10⁶ cycles, the cracks initiated from persistent slip bands found at the surface of the specimen. At lower stress levels, slip bands were developed without initiating the cracks. The horizontal asymptote S–N curve from 10⁶ to 10⁹ cycles was attributed to the development of slip bands all over the surface of the specimen, before crack initiation.     

相界面对核电Z3CN20-09M不锈钢裂纹萌生和扩展的影响

为研究国产核级主管道不锈钢Z3CN20-09M中奥氏体/铁素体相界面在裂纹萌生与扩展过程中的作用,通过扫描电镜原位拉伸技术对核级主管道不锈钢在拉伸过程中的组织形变、微裂纹的萌生与扩展进行原位观察,对断口进行了分析.研究表明,在拉伸过程中,微裂纹优先在杂质颗粒和相界位置萌生.当铁素体/奥氏体界面垂直于拉伸方向时,裂纹倾向于沿相界萌生,并沿相界扩展;当铁素体/奥氏体界面平行于拉伸方向时,微裂纹在相界开裂,并垂直于界面扩展,主裂纹发生偏折,界面在裂纹扩展过程中起阻碍作用.     

Effects of grain size on cyclic plasticity and fatigue crack initiation in nickel

Fatigue experiments were conducted on polycrystalline nickel of two grain sizes, 24 and 290 μm, to evaluate the effects of grain size on cyclic plasticity and fatigue crack initiation. Specimens were cycled at room temperature at plastic strain amplitudes ranging from 2.5×10⁻⁵ to 2.5×10⁻³. Analyses of the cyclic stress–strain response and evolution of hysteresis loop shape indicate that the back stress component of the cyclic stress is significantly affected by grain size and plastic strain amplitude, whereas these parameters have little effect on friction stress. A nonlinear kinematic hardening framework was used to study the evolution of back stress parameters with cumulative plastic strain. These are related to substructural evolution features. In particular, long range back stress components are related to persistent slip bands. The difference in cyclic plasticity behavior between the two grain sizes is related to the effect of grain size on persistent slip band (PSB) morphology, and the effect this has on long range back stress. Fine grain specimens had a much longer fatigue life, especially at low plastic strain amplitude, as a result of the influence of grain size on fatigue crack initiation characteristics. At low plastic strain amplitude (2.5×10⁻⁴), coarse grain specimens initiated cracks where PSBs impinged on grain boundaries. Fine grain specimens formed cracks along PSBs. At high plastic strain amplitude (2.5×10⁻³), both grain sizes initiated cracks at grain boundaries.     

Microstructural influence on small fatigue cracks in a ferritic–martensitic steel

Microstructure effects on fatigue crack initiation and propagation in ferritic–martensitic dual phase steel were investigated. Slip bands were formed in ferrite grains after several thousand cycles with ensuing crack initiation due to dislocation pile-up. Subsurface observations using a focused ion beam (FIB) and crystallographic analyses using electron backscatter diffraction (EBSD) measurements showed that crack initiation occurred as a result of the activation of a slip system having a high Schmid factor. Surface crack nucleation occurred quite frequently at ferrite/martensite and ferrite/ferrite boundaries, with crack propagation in the ferrite grains. This initiation mode can be attributed to the mismatch stresses at ferrite/martensite phase boundaries and at high angle grain boundaries.