共查询到19条相似文献,搜索用时 187 毫秒
1.
2.
3.
4.
通过结构分析、断口检查、硬度测试、抗拉试验、显微组织观察及能谱分析,对电厂高温再热器SA-213TP347H钢管进行裂纹原因分析。结果表明:高温再热器在运行中容易晃动,裂纹处于管夹挤压的凹坑;裂纹处管材的拉伸性能、硬度均符合ASME A213/A213M对SA-213TP347H钢的要求;显微组织为奥氏体和沿晶界分布的含Cr碳化物,裂纹是沿晶裂纹,由管外壁向管内扩展;裂纹处腐蚀产物均含有O、S等非金属元素。分析表明:产生裂纹的原因是由于管夹挤压管道,同时管道结构易晃动,增加了挤压变形处的应力,促进了含Cr碳化物沿晶界析出,形成贫Cr区而导致晶界弱化,并在腐蚀性介质的作用下,导致晶间应力腐蚀开裂。 相似文献
5.
某电厂600 MW亚临界机组12Cr1MoV钢末级再热器管运行51020 h后发生爆裂。采用光学显微镜、扫描电镜等设备,从宏观检查、氧化层检测、组织分析和能谱分析方面对失效管样进行研究。结果显示,爆口呈长期过热开裂宏观特征。管样向火侧氧化层过厚,组织球化严重。爆口处向火侧管壁存在明显的蠕变孔洞和沿晶裂纹,裂纹沿着晶界发展并充满氧化物。能谱分析结果显示,末级再热器管向火侧管壁在长期服役过程中,基体出现固溶合金元素贫化,导致组织劣化。综上,12Cr1MoV钢末级再热器管失效是由长期过热引起管件向火侧组织劣化、蠕变开裂造成的。 相似文献
6.
通过取样对某电厂失效水冷壁鳍片焊缝进行宏观观察、光谱分析、显微组织及能谱分析,试验结果表明:泄漏水冷壁管鳍片焊缝存在长度约为95 mm的富铜聚集区,w(Cu)达85.14%,鳍片焊缝富铜聚集区及其与管子母材过渡层存在沿晶小裂纹,裂纹内填充有黄褐色的铜质合金。水冷壁管鳍片焊缝失效原因为在埋弧焊过程中,铜质导电嘴与管子母材接触发生短路,短路电流产生的高温使导电嘴与管子母材接触部分熔化,管子母材局部被烧穿,铜合金熔入到焊缝金属中,低熔点富铜合金沿母材和焊缝晶界扩散,导致晶界脆化并产生裂纹,最终发生熔铜开裂。 相似文献
7.
以超超临界锅炉SA213?T23钢水冷壁失效管为试验对象,通过宏观检查、化学成分分析、金相检验和硬度试验,分析失效原因。结果表明:该水冷壁管化学成分正常,材质性能未发生明显劣化;水冷壁失效原因为鳍片焊缝开裂,该裂纹为沿晶界扩展的再热裂纹,起源于焊缝熔合线附近的热影响区粗晶区域,先沿热影响区横向扩展,然后扩展至母材区域,最终导致管壁泄漏失效;热影响区粗晶区域显微组织为粗大的马氏体和贝氏体组织,硬度明显偏高于焊缝熔合线另一侧的焊缝区域,脆性增大。两者在显微组织和硬度上的明显差别,使焊缝熔合线附近的热影响区粗晶区域容易产生应力集中,在高温运行中发生晶间开裂。 相似文献
8.
某火电厂锅炉在进行试验管屏风压试验测试时,发现再热器管(22Cr-15Ni钢)与套管(18Cr-8Ni-Nb钢)的密封焊接处存在裂纹,通过样管宏观分析、裂纹金相分析和断口及析出相的SEM/EDS分析了其裂纹产生原因。结果表明,失效处附近存在机械应力输入和焊瘤应力集中的明显痕迹,焊瘤热输入导致局部组织过热,同时基体M23C6球状析出相异常长大造成微观拉应力。上述原因的综合作用最终导致机械应力从应力集中处输入产生微裂纹,并沿着过热弱化的晶界扩展,与基体析出相产生的微裂纹汇合,最终扩展成为环向断口。风压泄漏吹击断口,造成断面上因热输入异常长大的M23C6球状析出相上产生韧性变形凹坑和脆性开裂, 并显露内部枝状晶的微观断口形貌。 相似文献
9.
10.
11.
通过对比热挤压成形管材和爆裂管材的组织以及对爆裂管材裂纹和断口的分析,研究了热挤压成形GH3625合金管材的组织及裂纹形成机理。结果表明:爆裂管材与成形管材的组织均为等轴晶,但爆裂管材的开裂使晶界处的应力集中得以释放,其组织中并没有形成变形孪晶,在管材径向方向上也不存在晶粒尺寸不均匀的现象。挤压比过高导致管材在热挤压过程中绝热升温严重,使低熔点的Laves相熔化并扩散到周围基体中,是裂纹形成的根本原因。在模具出口处高拉应力的作用下,这些裂纹不断扩展最终连接在一起,导致管材的爆裂现象。由于断口表面冷却速率较高,组织通过奥氏体区的时间较短,再结晶形核核心多且晶粒长大过程受阻,使断口表面形成了一层十分细小的再结晶晶粒。 相似文献
12.
HP40裂解炉管组织及裂纹产生原因分析 总被引:1,自引:0,他引:1
本文用SEM、EDS、XRD对开裂的HP40裂解炉管进行分析,发现多数裂纹均位于焊缝附近,且均沿枝晶间和晶界开裂的碳化物扩展.经EDS成分分析和XRD结构分析,这些开裂的碳化物为M23C6和富Nb、Si的碳化物.新炉管组织为奥氏体和枝晶间分布的M7C3及高Nb、Si的共晶碳化物.新旧炉管比较可知,开裂炉管的结构和形态在长时间高温下均发生了明显变化,即M7C3转变为M23C6且明显粗化,在晶界呈连续分布.这种脆而硬的碳化物在组织应力和热应力作用下碎裂成为潜在的裂纹源,它们加速了裂纹扩展进程,缩短了炉管的使用寿命.沿裂纹打开断口发现,整个断面被这两种碳化物所覆盖.这进一步证实了造成裂解炉管早期开裂的原因是这种沿晶界连续分布的粗大碳化物的存在. 相似文献
13.
14.
15.
Due to the practical limitations of lowering the diffusible hydrogen content of flux-containing welding consumables, it is
now felt that modification of the weld microstructure would alleviate the risk of weld metal cracking in multi-pass weld deposits.
Thus, this study aimed to identify and evaluate the effect of the weld microstructure on the cold cracking susceptibility
of FCAW weld metals and then to provide a basic guideline for designing new welding consumables from a microstructural point
of view. In order to identify the parameter(s) that can quantify the microstructural susceptibility of multi-pass weld deposit,
two sets of FCAW wires with tensile strength of about 600 MPa were prepared by controlling the Ni content to allow sufficient
variation in the weld microstructure, but with little change in weld metal strength. The cold crack susceptibility of those
two chemistries was evaluated by a multi-pass weld metal cracking test at various levels of diffusible hydrogen content. All
of the cold cracks developed were Chevron-type, and the occurrence of such cracks depended upon the proportion of grain boundary
ferrite (%GF) as well as the diffusible hydrogen (HD) content. In fact, at the same level of HD, higher Ni (1.5%Ni) wire showed
better resistance to cold cracking than lower Ni (0%Ni) wire even though the latter was stronger and also higher in carbon
equivalent. This result could be explained solely by the difference in grain boundary ferrite content between those two welds
since Chevron cracking preferentially initiates at and propagates along grain boundary ferrite. Therefore, we propose the
use of a value of %GF as a parameter to quantify the microstructural susceptibility of ferritic multipass weld deposit with
a strength level of about 600 MPa. It was further suggested that, in addition to the hydrogen control approach, microstructural
modification in the form of reducing the %GF can be pursued to develop welding consumables with improved resistance to cold
cracking. 相似文献
16.
The influences of microstructure and inclusion on cold cracking were studied in high-strength steel welds of YS 600?MPa grade using the Y-groove test. The weld microstructure showed a mixture of acicular ferrite, bainite and predominantly martensite. Cold crack fractography identified intergranular fracture (IF) and quasi-cleavage fracture (QCF). Bainite and martensite predominated on the surface and subsurface of IF while the QCF showed inclusions that nucleated acicular ferrite. The influence of inclusions on cold cracking can be described as follows: (i) the inclusions acted as nucleation sites of QCF, (ii) the inclusions contributed to the nucleation and growth of micro-cracks and (iii) new cracks were produced from inclusions when a crack impinged on the inclusions. Inclusions smaller than 2?μm increased the cold crack resistance by contributing to the nucleation of acicular ferrite. Inclusions larger than 2?μm increased the cold crack susceptibility by inducing crack nucleation in welds. 相似文献
17.
18.
Jae Hak Kim Jun Seok Seo Hee Jin Kim Hoi Soo Ryoo Ka Hee Kim Moo Young Huh 《Metals and Materials International》2008,14(2):239-245
The effect of microstructures on weld metal cold cracking has been studied using flux-cored are welding (FCAW) wires with
a 600 MPa strength level. Two FCAW wires were prepared by controlling the Ni content to allow a sufficient variation in weld
microstructures, but with little change in the weld metal strength. The microstructural analysis showed that there was a significant
difference in the proportions of the microstructural constituents of the weld microstructure. The 1.5%Ni wire resulted in
a weld microstructure with a lower grain boundary ferrite (GF) content associated with an increased proportion of acicular
ferrite (AF) than the 0% Ni wire. The GF contents of 0%Ni and 1.5%Ni weld metal were measured to be 19% and 6%, respectively.
The cold crack susceptibility of these two FCAW wires was evaluated using the gapped bead-on-plate (G-BOP) test at the two
different levels of diffusible hydrogen content As a result of the G-BOP tests, it was demonstrated that the 1.5%Ni wire had
better resistance to cold cracking than the 0% Ni wire because its weld deposit had a lower GF phase content. This implies
that, in addition to the hydrogen control approach, microstructural modification can be pursued to develop new welding consumables
with an improved resistance to cold cracking. In the discussion, the detrimental effect of GF against cold cracking is addressed
based on the microstructural characteristics of cold cracks in ferritic weld metal. 相似文献