离子注入Ce对Fe—23Cr—5Al合金上AI2O3膜生长应力的影响

利用双面氧化弯曲方法原位测量了Ｆｅ－２３Ｃｒ－５Ａｌ合金空气中氧化形成的ＡＩ２Ｏ３膜平均生长应力。ＡＩ２Ｏ３膜内存在压应力。９００℃下氧化２０ｈ,膜内应力从３．５降低到２ＧＰａ,１０００℃下氧化１０ｈ,膜内应力从０．８降低到０．４ＧＰａ,合金表面离子注入１×１０＾１７Ｃｅ＾＋／ｃｍ＾２,增大了ＡＩ２Ｏ３膜的生长应力,其原因是添加稀土促进膜的横向生长,离子注入Ｃｅ同时增大了合金的氧化速率,促进了ＡＩ     

Fe—23Cr—5Al合金1000^0C氧化形成的Al2O3膜生长应力研究

采用一种测定氧化膜生长应力的双面氧化弯曲方法,测量了Ｆｅ－２３Ｃｒ－５Ａｌ（Ｆｅ－２２．６Ｃｒ－．４２Ａｌ－０．２１Ｔｉ,ｗｔ％）合金在１０００＾０Ｃ空气中氧化形成的Ａｌ２Ｏ３膜的平均生长应力,研究了氧化膜应力释放机制,Ａｌ２Ｏ３膜的平均生长应力随膜厚增大而减小,其大小从－１ＧＰａ数量级变化到－１００ＭＰａ数量级。基体全金和Ａｌ２Ｏ３膜在１０００＾０Ｃ时均发生蠕变,合金氧化一定时间后于真空保温退火     

用双面氧化弯曲方法测定Al2O3膜生长应力

提出了一种测定氧化膜生长应力的双面氧化弯曲方法,经不象常规弯曲法那样为防止试样一个侧在发生氧化度制保护除层,因而可用于较高温度及较长时间的氧化情况并可测定Ａｌ２Ｏ３膜的生长应力,由于高温下合金及薄氧化膜发生蠕变,从而释放膜内应力。新方法应用于合金的蠕变数据,并采用数值计算来获得氧化膜应力值,用这种方法测定Ｆｅｃｒａｌｌｏｙ（Ｆｅ－２２Ｃｒ－５Ａｌ－０．３Ｙ）合金在１０００℃空气中氧化中形成的Ａｌ２     

表面施加氧化物薄膜涂层对Fe25Cr5Al合金高温氧化行为的影响

用电沉积－热解方法在合金表面获得了厚度为０．１－０．５μｍ的单一Ｙ２Ｏ３,Ａｌ２Ｏ３或不同Ｙ２Ｏ３含量与Ａｌ２Ｏ３或Ｃｒ２Ｏ３混合的氧化物薄膜涂层,研究了在１１００℃,１０＾４ＰａＯ２的条件下各类ＯＴＦＣ对Ａｌ２Ｏ３形成Ｆｅ２５Ｃｒ５Ａｌ合金恒温氧化和循环氧化行为的影响。     

溅射Ni-8Cr-3.5Al纳米晶涂层的抗高温氧化行为

对Ｎｉ－８Ｃｒ－３．５Ａｌ质量分数,％合金及其纳米晶涂层进行了１０００℃空气中高温氧化研究。结果表明：Ｎｉ－８Ｃｒ－３．５Ａｌ纳米晶涂层的抗高温氧化性能优于Ｎｉ－８Ｃｒ－３．５Ａｌ合金。这主要在于Ｎｉ－８Ｃｒ－３．５Ａｌ纳变涂层表面生成了具有分层结构含一连续α－Ａｌ２Ｏ３内层的氧化膜,而Ｎｉ－８Ｃｒ－３．５Ａｌ合金则生成了由Ｃｒ２Ｏ３内氧化物组成的氧化膜。讨论了涂层氧化膜的生成过程。     

Fe3Al基合金的高温氧化行为

测定了Ｆｅ３Ａｌ基合金铁静态和拉庆务态下的氧化增重曲线，并与０Ｃｒ２５Ａｌ５合金进行比较，结果表明，在较低温度下Ｆｅ３Ａｌ基合金的静态氧化性能不如０Ｃｒ２５Ａｌ５；当温度高于９００℃时，Ｆｅ３Ａｌ基合金的氧化性能要比０Ｃｒ２５Ａｌ５好。但Ｆｅ３Ａｌ基合金在拉应力作用下的动态氧化性能比０Ｃｒ２５Ａｌ５差。动态下合氧化增重不仅与和氧化时间有关，还与拉应力的大小有关。文中人这似的动态氧化△ｗ＝ｋ１ｔ＾２     

Ni—18Cr—3.5Al合金在Cl2—H2O环境中的高温腐蚀

研究了Ｎｉ－１８Ｃｒ－３．５Ａｌ合金在５６５℃Ｃｌ２－Ｈ２Ｏ混合气氛中的腐蚀行为，并用ＸＰＳ分析了腐蚀产物膜的结构。在高温Ｃｌ２－Ｈ２Ｏ环境中的腐蚀由Ｃｌ２、ＨＣｌ造成的氯化过程和Ｏ２、Ｈ２Ｏ等造成的氧化过程共同引起。在高温Ｃｌ２环境中低含量Ｈ２Ｏ加速腐蚀过程，而高含量Ｈ２Ｏ延缓腐蚀过程。     

Fe—Mn─Al合金的腐蚀性能与钝化膜的研究

应用阳极极化及ＡＥＳ／ＸＰＳ技术,研究了Ｆｅ－３０．８Ｍｎ－８．２Ａｌ奥氏体合金在ｐＨ值为－０．８至１５．３的水溶液中的腐蚀性能,并与Ｆｅ－３０Ｍｎ合金、低碳钢、９％Ｎｉ低温钢及１Ｃｒ１３不锈钢进行对比。在所测试的水溶液中,该合金的腐蚀抗力优于低碳钢和Ｆｅ－３０Ｍｎ合金,与９％Ｎｉ钢相当,但不及１Ｃｒ１３不锈钢。Ｆｅ－３０．８Ｍｎ－８．２Ａｌ合金在１ｍｏｌ／ＬＮａ２ＳＯ个中形成的钝化膜的最表层可能为氢氧化物,而膜的主体由Ｆｅ２Ｏ３、Ｍｎ２Ｏ３及Ａｌ２Ｏ３组成。     

Fe－Cr－Al合金在纯SO_2气氛中的高温热循环腐蚀行为

研究了Ｆｅ－２０Ｃｒ－５Ａｌ和Ｆｅ－２０ＣｒＳＡｌ－０．５Ｙ合金在１２００℃ｌａｔｍＳＯ２气氛中热循环条件下的高温腐蚀行为，并与恒温腐蚀相比较．测定了腐蚀动力学曲线，观察腐蚀产物表面，横截面和脆断断口的形貌，并分析元素的分布，确定腐蚀产物相组成．结果表明，在５０００小时实验周期内，不含钇的合金遭受氧化／硫化腐蚀，腐蚀动力学呈直线规律．含钇合金只发生高温氧化反应，腐蚀动力学与恒温腐蚀时的差别不大，仍大体符合抛物线规律．加钇有效地抑制了Ａｌ３＋在α－Ａｌ２Ｏ３中的扩散，合金表面氧化膜依赖氧的传质而成长，发展出粘着性好的柱状晶，在交变热应力作用下不易开裂和剥落，显著提高了合金的耐蚀性．     

氧化物薄膜促使镍铬合金高温选择氧化的研究

表面沉积Ｙ２Ｏ３薄膜可以促使Ｎｉ－１５％Ｃｒ合金在１０００℃中生成Ｃｒ２Ｏ３选择性氧化膜，氧化量下降约２０倍，而沉积Ａｌ２Ｏ３薄膜仅在较短的时间内使合金的局部表面生成Ｃｒ２Ｏ３选择性氧化膜。从沉积氧化物薄膜对Ｃｒ２Ｏ３氧化膜的生核及生长过程的作用，对氧扩散的阻挡作用，以及氧化物薄膜与Ｃｒ２Ｏ３氧化膜掺杂后引起氧化膜中传质过程和应力状态的变化，分析了氧化物薄膜促使镍铬合金在较低铬含量下发生高温选择氧     

DEFLECTION METHOD FROM TWO SIDES OXIDATION TO STUDY EFFECT OF Y ON INTERNAL STRESS OF OXIDE SCALES

Au investigation was carried ont of the effect of Y addition upon the internal stressof Al_2O_3 scale formed during oxidation of sputtering coating on Co-30Cr-6Al alloyand the growth stress of oxidized film on Fe-23Cr-5Al alloy heating up to 900℃ inair,using a specially designed deflection method from thin strip specimen with coat-ings,ion-implanted Y on one side and oxidized onto both sides.Results indicate thatY may decrease the internal stress of oxide scale on 2×10~(17) Y~+/cm~2 implanted Co-30Cr-6Al coating,and increase one on 2×10~(16) Y~+/cm~2 implanted Fe-23Cr-5Al alloy.This seems due to whether or not Y promotes the plastic deformation of oxide scale.Inaddition,at initial oxidation stage,the change of growth stress of oxide scale formed onY-implanted Co-30Cr-6Al coating may be related to the influence of Y on oxidationprocess of the coating.     

The isothermal oxidation behaviour of Fe-Cr-Al and Fe-Cr-Al-Y alloys at 1200°C

The isothermal oxidation kinetics of Fe-14Cr-4Al, Fe-27Cr-4Al and similar alloys containing 0.008, 0.023 and 0.8Y have been investigated in 1 atm. oxygen at 1200°C and related to the appropriate oxide morphologies and compositions. The yttrium-free alloys develop a convoluted oxide morphology, with significant areas of lost contact between the oxide and the alloy specimen surface, which results from lateral growth of the oxide and the development of high compressive growth stresses. These are due to oxide formation within the oxide where Al³⁺ ions diffusing outwards through the bulk oxide meet O^2? ions diffusing inwards along oxide grain boundaries. The additions of yttrium to the alloys reduce the oxide growth stresses and suppress the development of the convoluted oxide. This is reflected in the oxidation kinetics. During cooling, scale cracking and some spalling occurs for the yttrium-free alloys, due to the imposition of stresses, caused by the differential thermal contraction between the oxide and alloy, on the already highly stressed, partially detached oxide. Although the addition of 0.008Y to the alloy actually increases the amount of oxide spallation on cooling, further additions of 0.023Y or 0.8Y to the alloy reduce the oxide growth stresses, prevent scale detachment at temperature and thus reduce or prevent oxide damage on cooling.     

The influence of manganese on the High-temperature oxidation of iron-chromium alloys

An investigation has been undertaken into the oxidation behaviour of manganese-containing Fe-28% Cr alloys in oxygen at 800° and 1000°C. The presence of the tertiary element has a detrimental effect on the oxidation resistance, resulting in enhanced scale-growth rates during isothermal exposure and increased incidences of scale failure at temperature. This is largely due to relatively rapid rates of diffusion of manganese across the Cr₂O₃ scale and formation of MnCr₂O₄ spinel on its outer surface. The scale on Fe-28% Cr-1% Mn consists of a layer of Cr₂O₃, containing a small concentration of manganese, with an outer layer of the spinel oxide. During the early stages, an inner layer of the spinel also develops, but, eventually, this almost completely disappears as the manganese diffuses into the outer scale. A similar scale forms on Fe-26% Cr-5% Mn, but the higher manganese concentration enables a significant amount of this element to be retained in the inner regions. The overall growth rate of the scale is significantly faster than on Fe-28% Cr or the 1% Mn-containing alloy.     

Inhibition mechanism of S-containing additives towards intergranular corrosion of a sensitized stainless steel

The comparison of the polarization curves recorded on both pure Fe, Cr, Ni, and Fe-18Cr-8Ni, Fe-8Cr-8Ni alloys, and Fe-10Ni, Fe-17Cr alloys in 1 N H₂SO₄ at 70°C clarifies the mechanism of inhibition of IG corrosion on sensitized AISI 304 SS by S-containing additives. These additives stimulate the anodic dissolution process of Fe-18Cr-8Ni alloy and inhibit this process on Fe-8Cr-8Ni alloy. The anodic behaviour of Fe-18Cr-8Ni is similar to that of pure chromium, while the behaviour of Fe-8Cr-8Ni is similar to that of pure iron.     

The structure and adhesion of oxide scales on Fe?Ni?Mo and Fe?Cr?Mo alloys

The Structure and Adhesion of Oxide Scales on Fe? Ni? Mo and Fe? Cr? Mo Alloys A preliminary study has been made of the structure and adhesion of oxide scales formed on Fe-1.8 wt.% Ni-0.3wt.% Mo and Fe-1wt.% Cr-0.5wt.% Mo in oxygen at 930°–1250°C. From 930°–1250°C, the Fe? Ni? Mo alloy oxidised at a slower rate that the Fe? Cr? Mo alloy, and both alloys oxidised at a slower rate than high-purity iron. Hot bend tests and hot tensile tests of a scale-metal joint revealed that the scales comprised a strongly adherent inner layer (enriched in Cr? Mo or Ni) and a weakly coherent bulk structure. In the Fe? Ni? Mo alloy, failure in the bulk scale occured along a smooth plane at the edge of the Ni-enrichment zone whereas in contras, for the Fe? Cr? Mo alloy, failure occured withing the Cr? Mo enriched zone adjacent to the scale-metal interface.     

The Influence of KCl and HCl on the High-Temperature Oxidation of a Fe-2.25Cr-1Mo Steel at 400 °C

The influence of alkali- and chlorine-containing compounds on the corrosion of superheater alloys has been studied extensively. The current paper instead investigates the corrosive effects of KCl and HCl under conditions relevant to waterwall conditions. A low-alloy (Fe-2.25Cr-1Mo) steel was exposed to KCl(s), 500 vppm HCl(g) and (KCl?+?HCl) in the presence of 5%O₂ and 20% H₂O at 400 °C. The results indicate that alloy chlorination by KCl occurs by an electrochemical process, involving cathodic formation of chemisorbed KOH on the scale surface and anodic formation of solid FeCl₂ at the bottom of the scale. The process is accompanied by extensive cracking and delamination of the iron oxide scale, resulting in a complex, convoluted scale morphology. Adding 500 vppm HCl to the experimental environment (KCl?+?HCl) initially greatly accelerated the formation of FeCl₂ at the scale/alloy interface. The accelerated alloy chlorination is attributed to HCl reacting with KOH at the scale surface, causing the cathodic process to be depolarized. A rapid slowing down of the rate of chlorination and corrosion in KCl?+?HCl environment was observed which was attributed to the electronically insulating nature of the FeCl₂ layer which forms at the bottom of the scale, disconnecting the anodic and cathodic regions.

     

A preliminary study of the mechanics of scale detachment from an Fe-Cr-Mo alloy at elevated temperatures

The gradual detachment of a disc of scale from the surface of Fe-1% Cr-0.5% Mo alloys (with 0, 0.25 and 0.5% Si) oxidized in oxygen at 1050–1100°C, was recorded by a robot camera. An analytical model based on the rigid plastic theory of plate deformation was developed to calculate the energy dissipated during scale detachment. Preliminary results for the work of scale adhesion are for the 0% Si alloy: 42–54 Jm^?2; for the 0.25% Si alloy: 106–118 Jm^?2 and for the 0.5% Si alloy: 24–26 Jm^?2 at 1050°C.     

Criteria for the formation of protective Al2O3 scales on Fe-Al and Fe-Cr-Al alloys

The conditions for the formation of external alumina scales on binary Fe-Al alloys and the nature of the third-element effect due to chromium additions have been investigated by studying the oxidation at 1000 °C in 1 atm O₂ of a binary Fe-10 at.% Al alloy (Fe-10Al) and of two ternary Fe-Cr-10 at.% Al alloys containing 5 and 10 at.% chromium (Fe-5Cr-10Al and Fe-10Cr-10Al, respectively). An Al-rich scale developed initially on Fe-10Al was subsequently replaced by a multi-layered scale containing mixtures of Fe and Al oxides plus a large number of Fe-rich oxide nodules: internal aluminum oxidation was essentially absent from this alloy. Addition of 5 at.% chromium to Fe-10Al did not suppress the formation of nodules, but they were eventually healed by the growth of an alumina layer at their base, resulting in a significant reduction of the oxidation rate. Finally, the alloy with 10 at.% Cr formed continuous external alumina scales without any Fe-rich nodule. Thus, the addition of sufficient amounts of chromium to Fe-10Al produces a third-element effect as expected. However, the process found in this alloy system does not involve a prevention of the internal oxidation of Al. Instead, it shows a transition from the growth of mixed Fe- and Al-rich external scales directly to an external Al₂O₃ scale formation. An interpretation of this kind of mechanism involving a third-element is presented along with a prediction of the critical Al contents required to produce the various possible scaling modes on binary Fe-Al alloys.     

不同钒,碳含量高速钢的凝固组织及相组成

利用热分析，Ｘ射线衍射和着色金相法详细研究了Ｆｅ－５Ｃｒ－５Ｍｏ－Ｔ２－Ｖ－Ｃ系合金中Ｖ和以Ｃ量对凝固过程中结晶相的种类和结晶温度的影响，得到了合金万分与凝固组织的关系，建立了（Ｆｅ－５Ｃｒ－５Ｍｏ－５Ｗ－２Ｃ）－Ｖ和（Ｆｅ－５Ｃｒ－５Ｍｏ－５Ｗ－３Ｖ）－Ｃ的准二元相图，以及（Ｆｅ－５Ｃｒ－５Ｍｏ－５Ｗ）－Ｖ－Ｃ合金的液相面投影图。     

The interactions of sulphidation and particle erosion at high temperatures

Although there have been many studies of erosion-corrosion of alloys involving impact by solid particles in air or oxygen at high temperatures, there have been very few, if any, in gases of high-sulphur, low-oxygen activities. As these environments are pertinent in processes such as coal gasification and catalytic cracking of oil, there is a need for some basic studies of the interactions of erosion and corrosion in oxidizing/sulphidizing gases. Thus, a whirling-arm rig has been designed and constructed; it can operate under a range of erosion conditions (velocities to 30 m s⁻¹, particles fluxes to 1 g m⁻² s⁻¹) in gaseous environments consisting of mixtures of nitrogen, hydrogen, hydrogen sulphide and water vapour as necessary, at temperatures to 800°C. Some preliminary tests have been carried out using 310 stainless steel and Alloy 800HT at 500 and 700°C and Fe-2.25Cr-1 Mo and 410 stainless steel at 500°C. Erosion particles were 25 μm alumina, with impact velocities of 10 to 25 m s⁻¹ and fluxes of 0.06 to 0.16 g cm⁻² s⁻¹. The gaseous environment was a mixture of hydrogen, hydrogen sulphide and nitrogen; this caused sulphidation of all the alloys at both temperatures. The extents of erosion-corrosion damage were determined by thickness-change measurements taken every 5 h and overall metal-recession measurements taken at the end of the full test period of 35 h. The extents of damage were increased significantly with increasing impact velocity for the austenitic alloys at 700°C; similar trends were observed at 500°C for Fe-2.25Cr- 1 Mo and 410 stainless steel, although the presence of impacting particles had only a small effect on the austenitic alloys at the lower temperature. These initial results are discussed in terms of the interactions of growth of the sulphide scale and removal of scale by the particles.