G18CrMo2-6钢在高温回火过程中第二相的演变

应用扫描电子显微镜、透射电子显微镜和能谱技术等手段研究了G18CrMo2-6钢正火组织中第二相在680℃下保温一系列时间段的转变。结果表明,在正火后贝氏体中析出相主要为马氏体/奥氏体(M/A)组元和合金渗碳体(M_3C);在回火保温初期M/A分解为铁素体(α)与M3C组织,随着保温时间延长M3C逐渐球化并溶解,M_(23)C_6在晶界析出并长大,同时基体上有细小弥散的MC相析出。即回火保温过程中组织随时间的延长发生M/A→α+M_3C,M_3C→M_(23)C_6+MC的变化。     

奥氏体热作工具钢的析出与强化

透射电镜(TEM)分析表明,奥氏体热作工具钢的强化相为晶内析出的MC,它与基体存在严格的晶体学取向关系:(111)_(MC)//(111)γ,[110]MC//[110]γ。在700℃时效,MC质点主要在基体中的空位上形核和长大;在800℃时效,MC质点同时在位错网和空位上形核和长大。晶界上存在两种碳化物:M_(23)C_6和M_7C_3。在700℃时效,M_(23)C_6与基体没有取向关系,而在800℃时效,这种碳化物与基体的取向关系为:(111)M_(23)C_6//(111)γ,[110]M_(23)C_6//[110]γ。     

GH118合金中σ相的X射线定量测定

σ相在显微镜下呈针状,如果深腐蚀,在扫描电镜中观察呈片状(见图1)。通常认为它是一种脆性相,当它的含量达到一定值时会降低合金的冲击强度、持久强度、蠕变强度和蠕变塑性。经X射线定性测定,在GH118合金中,标准处理(1190℃×1.5小时,空冷, 1100℃×6小时,空冷)后经750℃时效处理(500小时),σ相为痕迹,但时效时间增加到3000小时,σ相便大量析出。由于M_(23)C_6相和σ相的化学性能及电化学行为极为相似,用化     

700℃超超临界机组用617B镍基合金的组织结构和析出相

使用扫描电子显微镜(SEM)和透射电子显微镜(TEM)对比分析了617B镍基合金在750℃持久试样和时效态试样的组织结构和析出相。结果表明:在蠕变和时效过程中在晶内和晶界都析出复杂面心立方结构的M23C6,晶内析出有序立方结构γ′相,前者为多边形或条形,后者为粒状;随着试验时间的延长析出物的颗粒尺寸出现长大的趋势;应力对γ′相的生长影响不明显,但是对晶界碳化物有明显的影响;在长时间应力条件下,M23C6碳化物聚集长大。     

18Cr10NiNb耐热钢析出相的热力学计算和平衡相分析

将18Cr10NiNb耐热钢在650℃进行10,000h的时效试验,用扫描电镜和透射电镜分析了18Cr10NiNb奥氏体耐热钢的组织,通过热力学计算研究了500-1400℃碳、铌和氮含量的变化对平衡析出相的影响。结果表明:在18Cr10NiNb钢的时效过程中在晶内析出了富Nb的MX相,在晶界析出了富Cr的M_(23)C_6相。根据热力学计算,其平衡析出相为MX,M_(23)C_6和σ相。MX相和M_(23)C_6型碳化物的最高溶解温度分别约为1340℃和840℃。MX相的数量随C和Nb含量的提高而增加。σ相的数量随着C含量的提高而减少。添加0.2%的N元素后,MX相为含有N、Nb、Cr和少量C的复杂碳氮化物,且在其平衡组织中出现了Cr_2N相。     

5Cr21Mn9Ni4N钢锻造裂纹的研究

过高的锻造加热温度(1220℃)使冷却时形成大量晶界枝晶片状M_7C_3,造成晶界严重弱化;在1200℃以下加热后的冷却过程中,晶界和惯析面上均形成一定数量的片状M_(23)C_6,且随着温度的降低钢的最薄弱环节由晶界向晶内转移.晶界和晶内惯析面的弱化,易导致锻坯、尤其是锻坯表面形成裂纹.确定了合适的锻造温度参数.     

基于微观组织演化的P91钢长时蠕变寿命预测

通过对P91耐热钢在高温长时蠕变过程中微观组织演化行为的综合考察,探讨了影响其长时蠕变寿命的主要因素,其中包括强化相(M_(23)C_6、MX)与析出相(Laves、Z相)的粗化现象以及和位错间的交互作用等。在此基础上,通过对蠕变幂率本构方程中耦合相应内应力参量,并结合Monkman-Grant方程,从微观组织演化的角度建立了P91耐热钢长时蠕变寿命预测模型。最后利用该模型对873K(600℃)时的P91耐热钢的相关蠕变寿命进行了预测,结果显示其计算数值与实验数据吻合较好,从而进一步表明基于微观组织演化的预测模型在P91耐热钢长时蠕变寿命的研究中具有重要意义。     

FGH95粉末镍基合金的组织结构与蠕变断裂特征

通过对不同工艺处理FGH95合金进行组织形貌观察及持久性能测试,研究了组织结构对合金持久性能的影响规律。结果表明:经1150℃固溶和时效处理后,合金中有粗大γ′相在较宽的边界区域不连续分布,其周围存在γ′相贫化区;经1160℃固溶及时效处理后,合金中粗大γ′相完全溶解,在晶内弥散分布高体积分数的γ′相,并有粒状(Cr,Nb)23(C,B)6硼碳化合物在晶内及沿晶界不连续析出;经1165℃固溶和时效后,合金的晶粒尺寸明显长大,并有硬而脆的碳化物膜沿晶界连续析出。在650℃、1034MPa条件下,经1160℃固溶和时效合金具有较高蠕变抗力和较长持久寿命,蠕变期间的变形机制是位错以Orowan机制饶过γ′相、或位错剪切γ′相,其中晶界处不连续析出的粒状碳化物可有效阻碍位错滑移,是使合金具有较好蠕变性能的主要原因。蠕变后期,合金的变形特征是晶内发生单取向滑移,随蠕变进行位错在晶界处塞积,并引起应力集中,致使裂纹在晶界处萌生及扩展是合金的蠕变断裂机制。     

热轧态Inconel690合金中碳化物的溶解和析出

研究了热轧态690合金中碳化物的溶解和析出行为及其结构,结果表明:在热轧态合金中存在的碳化物多数沿晶界长条状分布,少量呈颗粒状分布于晶内,类型为M_(23)C_6.热轧态合金的晶界和晶内碳化物的完全固溶温度分别为1050℃、1080℃,在低固溶温度下未完全溶解的残余晶界碳化物直接导致后续TT处理晶界不再析出碳化物;将合金完全固溶处理后,在后续TT处理的晶界上会重新析出细小、半连续的碳化物.     

1Cr12Ni2WMoVNb（GX—8）钢的回火转变研究

本文叙述了1Cr12Ni2WMoVNb(GX—8)钢的回火转变机制的研究结果。该钢经300℃回火析出Fe_3C型碳化物,400～500℃回火析出M_7C_3与M_2X,500～600℃回火析出M_2X和M_(23)C_6,600℃以上回火析出M_(23)C_6。由于在不同温度下回火,析出的碳化物类型、形态、数量和分布的不同,因而使钢具有不同的物理、力学和化学性能。     

Formation of Re-containing Carbides in a Second Generation Directionally Solidified Ni Base Superalloy

The precipitates at grain boundary in a directionally solidified Ni base superalloy after heat treatment, aging at 975℃, and creep rupture test have been characterized. Besides the primary MC carbides and fine particles of μ phase, the Re-containing M23C6 was observed. The precipitation kinetics revealed that the formation of M23C6 was associated with the dissolution of μ phase and MC carbides. TEM image shows that the continuous precipitation of M23C6 particles effectively hinders the dislocation movement ...     

Investigation and improvement on structural stability and stress rupture properties of a Ni–Fe based alloy

The structural stability and stress rupture properties of a Ni–Fe based alloy, considered as boiler materials in 700 °C advanced ultra-supercritical (A-USC) coal-fired power plants, was studied. Investigation on the structural stability of the existing alloy GH984 shows that the most important changes in the alloys are γʹ coarsening, the γʹ to η transformation and the coarsening and agglomeration of grain boundary M₂₃C₆ during thermal exposure. The stress rupture strength was found to be slightly lower than the requirement of 700 °C A-USC. The fracture mode of creep tested specimens was intergranular fracture. Detailed analysis revealed that η phase precipitation is sensitive to Ti/Al ratio and can be suppressed by decreasing Ti/Al ratio. The coarsening behavior of γʹ phase is related to Fe content. Adding B and P was suggested to stabilize M₂₃C₆ and increase grain boundary strength. Based on the research presented and analysis of the data, a modified alloy was developed through changes in composition. For the modified alloy, η phase is not observed and M₂₃C₆ is still blocky and discretely distributes along grain boundary after thermal exposure at 700 °C for 20,000 h. Moreover, the creep strength is comparable to the levels of Ni-based candidate alloys for 700 °C A-USC.     

Microstructure evolution and stress rupture properties of K4750 alloys with various B contents during long-term aging

The relationship among B content,microstructure evolution and stress rupture properties of K4750 alloy during long-term aging were investigated.After aging at 800 ℃ for 1000 h,the decomposition degree of MC carbides of K4750 alloys with 0B,0.007 wt.％ B and 0.010 wt.％ B were basically identical,which indicated that B has no inhibition on MC carbide decomposition during long-term aging.The MC carbide decomposition was accompanied by the formation of M23C6 carbides and a small number of η phases,which was controlled by the outward diffusion of C and Ti combined with the inward diffusion of Ni and Cr from the γ matrix.In addition,M23C6 carbides in boron-free alloy were in continuous chain and needle-like η phases were precipitated near them,while M23C6 carbides in boron-containing alloys remained in granular distribution and no η phases precipitation around them.Adding B could delay the agglomeration and coarsening of M23C6 carbides during long-term aging,which was because the segregation of B at grain boundary retarded the diffusion of alloy elements,thus weakened the local fluctuation of chemical composition near grain boundary.The stress rupture samples of K4750 alloys with various B contents after aging at 800 ℃ for 1000 h were tested at 750 ℃/380 MPa.The results indicated that the stress rupture properties of boron-containing alloys were significantly better than that of boron-free alloy,which could be attributed to the increase of grain boundary cohesion strength and the optimization of M23C6 carbide distribution due to the addition of B.     

On the microstructural origin of premature failure of creep strength enhanced martensitic steels

The creep strength enhanced martensitic steels are key material for the main power generating units in ultra-supercritical plants.Studies on the evaluation of their creep rupture life show there is an over-estimation of rupture life after long-term creep,which is known as premature failure.However,the microstructural origin of the premature failure remains unclear.Here in this study,we have carefully investigated the microstructural transformations and their influences on creep rupture behavior,showing that the evolution of martensite and M23C6 carbides as well as Laves phase are responsible for the pre-mature failure.By using multi-step TTP-LMP method,we confirmed a three-stage creep rupture behavior under different stress regions.Further quantitative analysis showed that the coarsening of M23C6 carbides and recovery of martensite exert equal and dominant effects on the premature failure in the medium stress region,while precipitation and coarsening of Laves phase are responsible for the premature failure in the low stress region.     

Effect of W–Mo balance on long-term creep life of 9Cr steel

The effect of tungsten–molybdenum (W–Mo) balance on creep life has been investigated for five heats of martensitic 9Cr steel with 1.5 % Mo equivalent (= 1/2W + Mo) at 600, 650 and 700°C. The combination of W and Mo concentrations in the present steel is 3W–0Mo, 2.8W–0.1Mo, 2.4W–0.3Mo, 1.8W–0.6Mo and 0W–1.5Mo. The time to rupture t_r exhibits a monotonous increase with increasing the W–Mo balance parameter 1/2W/(1/2W + Mo), namely, with increasing W concentration and concomitantly with decreasing Mo. The increase in t_r with increasing 1/2W/(1/2W + Mo) becomes less significant at long times. The precipitation of Fe₂(W,Mo) Laves phase takes place preferentially at prior austenite grain boundaries during creep, which enhances the grain boundary (GB) precipitation hardening. The amount of Laves phase increases with increasing 1/2W/(1/2W + Mo). The coarsening of Laves phase takes place at long times during creep, which reduces the GB precipitation hardening.     

Dissolution of laves phase by re-austenitization and tempering of creep strength enhanced ferritic steel

ABSTRACT

Formation of Laves phase in creep strength enhanced ferritic steel is investigated using re-austenitization and tempering treatment. The as-received material is exposed to 620°C for 4560?h aging, and then re-austenitizated at 1050°C for 1?h, and followed by tempering at 760°C for different times (2 and 4?h). After re-austenitization and tempering, the dissolution of Laves phase is observed while grain size and microhardness have not changed significantly. A model is suggested to quantify the dissolution of W-containing Laves phase. Thermo-Calc is used to predict driving forces for precipitation of Laves and M23C6 phases.     

Precipitate design for creep strengthening of 9% Cr tempered martensitic steel for ultra-supercritical power plants

Abstract

It is crucial for the carbon concentration of 9% Cr steel to be reduced to a very low level, so as to promote the formation of MX nitrides rich in vanadium as very fine and thermally stable particles to enable prolonged periods of exposure at elevated temperatures and also to eliminate Cr-rich carbides M₂₃C₆. Sub-boundary hardening, which is inversely proportional to the width of laths and blocks, is shown to be the most important strengthening mechanism for creep and is enhanced by the fine dispersion of precipitates along boundaries. The suppression of particle coarsening during creep and the maintenance of a homogeneous distribution of M₂₃C₆ carbides near prior austenite grain boundaries, which precipitate during tempering and are less fine, are effective for preventing the long-term degradation of creep strength and for improving long-term creep strength. This can be achieved by the addition of boron. The steels considered in this paper exhibit higher creep strength at 650 °C than existing high-strength steels used for thick section boiler components.     

Simulations of Coarsening Behavior for M23C6 Carbides in AISI H13 Steel

Based on the local equilibrium assumption, coarsening behavior of M23C6 carbide at 700℃ in H13 steel was simulated by DICTRA software. The results from the calculations were compared with transmission electron microscopy (TEM) observations. The results show the interfacial energy for M23C6 in H13 steel at 700℃ is thus probably 0.7 J·m-2, which fits the experiments well. The influence of composition and temperature on the coarsening rate was also investigated by simulations. Simulations show a decrease in the coarsening rate when V/Mo ratio is increased, while the coarsening rate increases with increasing temperature.     

Microstructural Evolution of 2.25Cr-1.6W-V-Nb Heat Resistant Steel during Creep

2.25Cr-i.6W-V-Nb developed in Japan, is a low alloy heat resistant steel with good comprehensive properties. Influence of long term creep at elevated temperature on the structure of 2.25Cr-I.6W-V-Nb steel was studied in this paper, and the micromechanism of creep strength degradation was elucidated, too. Both TEM observation and thermodynamic calculation reveal that during creep the transformation occurs from M7C3 and M23C6 to M6C, which can be cavity nucleation sites. Besides, creep at 600℃ also leads to the decrease of dislocation density, the coarsening and coalescence of M23C6, the nucleation of cavities and development of cracks. The strength decrease of 2.25Cr-1.6W-V-Nb steel after long term creep is related to the decrease of dislocation hardening,precipitation hardening,solution hardening,the nucleation of cavities and development of cracks.     

Creep rupture behaviour of modified 9Cr-1Mo heat-resistant steel strengthened with different mechanisms

The creep rupture behaviours and microstructural changes of a modified 9Cr-1Mo heat-resistant steel were investigated at 853 K. Analysis of creep results suggests that dislocation climb is the dominant deformation mechanism with true stress exponent of 5 under the present conditions. Based on the microstructural analysis, strengthening contributions from M₂₃C₆ carbides and MX carbonitrides were clarified. The M₂₃C₆ carbides can promote grain boundary strengthening by exerting Zener pinning forces, whereas MX carbonitrides can enhance the creep strength by interacting with mobile dislocations to induce threshold stress. Besides, softening of the steel is related not only to the decrease of dislocations, but also the coarsening of precipitates and substructures. The value of creep damage tolerance factor is close to 6.6, which further confirms that the creep damage is mainly attributed to the microstructural degradations, such as the coarsening of precipitates and substructures and decrease of dislocations.