罐体用3104大铸锭均匀化过程中的组织性能演变

采用金相、扫描电镜、透射电镜、显微硬度测试等方法对3104合金大尺寸铸锭的均匀化制度进行研究.研究结果表明:在均匀化过程中,晶粒内部析出大量Al(Mn,Si)相和Al(Mn,Fe,Si)相;铸锭表面区域的析出相分布较均匀,而铸锭中部经过580℃/(4～12 h)均匀化后的析出相分布不均匀,晶界和晶粒中心存在无析出带,析出相细小;随着温度升高,析出相分布更加均匀,密度降低,粒度长大;铸锭晶粒内部的初始显微硬度不均匀,经过均匀化处理,晶粒边界硬度下降,而晶粒中心硬度上升,显微硬度差别减少;经过600℃/(8～12 h)均匀化,显微硬度最低,且最均匀;铸锭均匀化处理对后续的再结晶退火有显著影响,铸锭经过600℃/12 h均匀化,与经过450℃/12h相比,后续冷轧产品经过再结晶退火后具有更高的延伸率,晶粒更细小均匀;合适的均匀化处理制度为600℃/(8～12 h).     

经济型双相不锈钢2101中氮化物在基体中的平衡固溶度计算

为了解析出物对经济型双相不锈钢2101热塑性的影响机制,对比了相同工艺下2101和2205双相不锈钢在热变形过程中相界析出物产生的规律.结果表明:2101钢比2205钢的相界处更倾向于产生析出物,促使后续热变形过程中相界产生裂纹,进而影响材料的热塑性.根据热力学相关数据,通过Thermo-Calc和实验测试数据,推导出2101和2205双相不锈钢析出物Cr2N的平衡固溶度公式,计算实验钢中析出物Cr2N的全固溶温度,同时引入Wagner相互作用系数,考虑了Ni、Mn、Mo和Si对固溶度积公式的影响.发现2101双相不锈钢中Cr2N的全固溶温度比2205钢高100℃左右,计算结果和实验结果吻合较好.实际生产过程中必须控制双相不锈钢热轧的终轧温度到全固溶温度以上,否则相界容易产生氮化物析出,影响材料热塑性.     

低频电磁场频率对半连铸高强Al合金组织结构的影响

利用光学显微镜和透射电镜研究了在低频电磁场作用下,电磁场频率对半连铸直径100mm铝合金铸锭显微组织结构的影响·结果表明:与常规铸锭相比,当电流为100A,频率为15Hz时,晶粒尺寸有所减小,并且等轴晶数目增多·当频率增到25Hz时,晶粒细化最明显·随频率继续增大,晶粒尺寸又有所增大;在电流为100A,电磁场频率为25Hz时,晶内位错密度较高,沉淀相尺寸较小,析出相主要为颗粒状的η′,η相和小片状的T相,此时晶界两侧无析出带宽度为100nm左右;当电磁场频率为15Hz时,晶内沉淀相尺寸有所增大,析出相主要为片状和长板条状的η相、片状的T相和颗粒状的η′相,晶界两侧无析出带宽度增到300nm左右...     

超声处理对2219大规格铝锭微观组织与宏观偏析的影响

在半连续铸造过程中施加超声,成功制备了Φ1250 mm 2219铝合金铸锭.利用光学显微镜、扫描电镜、能谱仪及直读光谱仪等仪器对铸锭的组织与成分分布进行检测与分析,探究超声对铸锭组织与偏析的内在作用机制.研究结果表明:超声振动引起的空化和声流效应能明显均匀组织结构,细化晶粒,尤其是心部晶粒细化率达到39.6%.超声促进铸锭晶间第二相呈枝丫状断续分布,晶内析出物点状弥散分布.同时,超声有效减小近表面负偏析,降低边部与心部之间的溶质浓度差异,弱化整个横截面的浓度波动,从而改善宏观偏析.     

WC晶粒度不同的双层硬质合金中的梯度结构

以晶粒度不同的2种WC粉末为原料,制备双层硬质合金试样.研究结果表明:在试样的层界面附近,出现过渡显微组织,其WC晶粒度、硬度呈现梯度分布,细晶层一侧的WC晶粒粗化,Co相平均自由程增大,硬度下降;粗晶层一侧的硬度上升;合金两侧的WC颗粒均处于非平衡状态.液相烧结时,界面两侧都有从外界吸入液态钴相以便使WC颗粒达到平衡状态的趋势,由于溶解-析出机制的作用,细晶侧的WC颗粒溶解后通过界面在粗晶侧的WC颗粒上析出,从而使粗晶侧的WC长大并达到平衡状态;与粗晶侧的WC相比,细晶侧的WC颗粒处于更加不稳定的状态,因此,粗晶侧的液态钴相流向细晶侧,使细晶侧的WC骨架发生重组而达到稳定状态.     

Q1030焊接高强钢的奥氏体晶粒异常长大机理

研究了Q1030钢在不同加热温度下的奥氏体晶粒长大现象.在一定温度范围内加热时,Q1030钢的部分奥氏体晶粒异常长大而出现混晶现象.分析了位于不同位置的析出相粒子对阻碍奥氏体晶粒长大的作用,用热力学方法计算不同加热温度下析出相粒子的大小和体积分数,并得出了析出相粒子钉扎阻力随加热温度的变化关系.结果表明,在一定温度范围内钉扎阻力迅速减小,导致部分晶粒异常长大,产生混晶现象.     

49MnVS3非调质钢连铸方坯中心裂纹分析

采用金相、扫描电镜及能谱分析了连铸方坯中心位置的宏观和微观特征．发现偏析是导致中心裂纹产生的主要原因,裂纹发生在柱状晶末端和粗大等轴晶区,沿一次枝晶晶界展开;开裂方式为沿晶开裂,开裂时期处于液相．存在两种晶界偏析,一种为析出的MnS夹杂物,另一种为聚集的浓化钢液．中心位置析出物未达到非调质钢质量要求．     

超重力场和稀土La变质对Al-14.5Si合金组织及硬度的影响

利用超重力场凝固技术和稀土La变质方法制备Al-14.5Si合金铸锭,研究了3000g超重力场下La含量对Al-14.5Si合金组织及硬度的影响。结果表明,3000g超重力场下凝固的Al-14.5Si合金铸锭主要分为边部和芯部两个区域。芯部占主要部分(14～16mm),在水平和垂直方向的组织都较为均匀,为超细共晶硅组织;边部厚度约为2～3mm,组织共晶硅较为粗大。水平方向上,铸锭显微硬度波动较大,中心区域最高;垂直方向上铸锭显微硬度波动较小。随着La含量的增加,共晶硅尺寸呈现先降低后增加的趋势,当La含量为0.6%时,晶粒细化程度最高,芯部共晶硅尺寸最小,平均直径约为0.25μm,平均长度约为0.37μm;芯部显微硬度随La含量增加呈先增加后降低的趋势,当La含量为0.4%时,铸锭芯部平均硬度最高可达HV91,相较普通重力场下未变质合金提升了48.2%。由此可见,超重力和稀土La变质对Al-14.5Si合金芯部共晶组织的细化及硬度的提升起到正协同作用。     

汽轮机高温镍基合金螺栓断裂原因分析

对靖远第二发电有限公司汽轮机GH4145/SQ高温镍基合金断裂螺栓利用扫描电子显微镜、光学显微镜等进行了分析研究.断裂螺栓晶粒粗大,有严重的混晶现象,碳化物及其他夹杂物在晶界呈链状或团状析出,使晶界脆化、晶界结合力下降而产生沿晶裂纹,导致螺栓发生沿晶脆性断裂.另外,螺栓在检修中出现表面损伤或受较大的预紧力也是螺栓断裂的另一原因.     

不同工艺下Nb-Ti微合金钢组织演变和析出行为

利用Gleeble 3800热模拟实验机、透射电镜和纳米压痕仪器等研究了终冷温度和保温时间对Nb-Ti微合金钢组织、析出行为的影响规律.结果表明:随终冷温度的升高,铁素体晶粒尺寸增大,珠光体增多,贝氏体逐渐减少,维氏显微硬度随终冷温度先升高后降低,当终冷温度为640℃时,实验钢的维氏显微硬度最大;当终冷温度为640℃时,试样中存在排列规则的相间析出和弥散分布的随机析出两种析出形式.当保温时间为0s时,析出物以相间析出和弥散析出为主;当保温时间为100s时,析出物以弥散析出为主.随保温时间增加,实验钢的纳米硬度降低了140MPa.     

A Cu-Cr alloy with nano and microscale Cr particles produced in a water-cooled copper mold

Microstructures have profound effects on the hardness and strength of Cu-Cr alloys. The microstructures of a Cu-Cr alloy cast in a water-cooled copper mold were studied in the present work. The scanning electron microscopy (SEM) results show that there are the copper matrix saturated with chromium, spherical precipitates of chromium separated from liquid phase during cooling before the initiation of solidification, and a eutectic phase in grain boundary areas. To investigate the effect of age-hardening treatment on the microstructures and properties of the material, some samples were subsequently age-hardened in a salt bath and investigated by transmission electron microscopy (TEM). The results show that coherent precipitates with the diameter of 11 nm are detectable in the samples before and after the age-hardening stage. Of course, the volume fraction of coherent precipitates is higher after the aging process.     

Characteristics of inclusions in high-Al steel during electroslag remelting process

The characteristics of inclusions in high-Al steel refined by electroslag remelting (ESR) were investigated by image analysis, scanning electron microscopy (SEM), and energy-dispersive spectrometry (EDS). The results show that the size of almost all the inclusions observed in ESR ingots is less than 5 μm. Inclusions smaller than 3 μm take nearly 75% of the total inclusions observed in each ingot. Inclusions observed in ESR ingots are pure AlN as dominating precipitates and some fine spherical Al₂O₃ inclusions with a size of 1 μm or less. It is also found that protective gas operation and slag deoxidation treatment during ESR process have significant effects on the number of inclusions smaller than 2 μm but little effects on that of inclusions larger than 2 μm. Thermodynamic calculations show that AlN inclusions are unable to precipitate in the liquid metal pool under the present experimental conditions, while the precipitation of AlN inclusions could take place at the solidifying front due to the microsegregation of Al and N in liquid steel during solidification.     

Mechanism of hot-rolling crack formation in lean duplex stainless steel 2101

The thermoplasticity of duplex stainless steel 2205 (DSS2205) is better than that of lean duplex steel 2101 (LDX2101), which undergoes severe cracking during hot rolling. The microstructure, microhardness, phase ratio, and recrystallization dependence of the deformation compatibility of LDX2101 and DSS2205 were investigated using optical microscopy (OM), electron backscatter diffraction (EBSD), Thermo-Calc software, and transmission electron microscopy (TEM). The results showed that the phase-ratio transformations of LDX2101 and DSS2205 were almost equal under the condition of increasing solution temperature. Thus, the phase transformation was not the main cause for the hot plasticity difference of these two steels. The grain size of LDX2101 was substantially greater than that of DSS2205, and the microhardness difference of LDX2101 was larger than that of DSS2205. This difference hinders the transfer of strain from ferrite to austenite. In the rolling process, the ferrite grains of LDX2101 underwent continuous softening and were substantially refined. However, although little recrystallization occurred at the boundaries of austenite, serious deformation accumulated in the interior of austenite, leading to a substantial increase in hardness. The main cause of crack formation is the microhardness difference between ferrite and austenite.     

Effects of aging on the microstructure of a Cu-Al-Ni-Mn shape memory alloy

The influence of aging on the microstructure and mechanical properties of Cu-11.6wt%Al-3.9wt%Ni-2.5wt%Mn shape memory alloy (SMA) was studied by means of scanning electron microscopy (SEM), transmission electron microscopy (TEM), X-ray diffractometer, and differential scanning calorimeter (DSC). Experimental results show that bainite, γ_2, and α phase precipitates occur with the aging effect in the alloy. After aging at 300dgC, the bainitic precipitates appear at the early stages of aging, while the precipitates of γ₂ phase are observed for a longer aging time. When the aging temperature increases, the bainite gradually evolves into γ₂ phase and equilibrium α phase (bcc) precipitates from the remaining parent phase. Thus, the bainite, γ₂, and α phases appear, while the martensite phase disappears progressively in the alloy. The bainitic precipitates decrease the reverse transformation temperature while the γ₂ phase precipitates increase these temperatures with a decrease of solute content in the retained parent phase. On the other hand, these precipitations cause an increasing in hardness of the alloy.     

A coupled model of TiN inclusion growth in GCr15SiMn during solidification in the electroslag remelting process

TiN inclusions observed in an ingot produced by electroslag remelting (ESR) are extremely harmful to GCr15SiMn steel. There-fore, accurate predictions of the growth size of these inclusions during steel solidification are significant for clean ESR ingot production. On the basis of our previous work, a coupled model of solute microsegregation and TiN inclusion growth during solidification has been estab-lished. The results demonstrate that compared to a non-coupled model, the coupled model predictions of the size of TiN inclusions are in good agreement with experimental results using scanning electron microscopy with energy disperse spectroscopy (SEM-EDS). Because of high cooling rate, the sizes of TiN inclusions in the edge area of the ingots are relatively small compared to the sizes in the center area. Dur-ing the ESR process, controlling the content of Ti in the steel is a feasible and effective method of decreasing the sizes of TiN inclusions.     

Effect of long-term service on the precipitates in P92 steel

The precipitates in P92 steel after long-term service in an ultra-supercritical unit were investigated by field-emission scanning electron microscopy and transmission electron microscopy and were found to mainly consist of M₂₃C₆ carbides, Laves phase, and MX carbonitrides. No Z-phase was observed. M₂₃C₆ carbides and Laves phase were found not only on prior austenite grain boundaries, martensite lath boundaries, and subgrain boundaries but also in lath interiors, where two types of MX carbonitrides—Nb-rich and V-rich particles—were also observed but the “winged” complexes were hardly found. Each kind of precipitate within the martensite laths exhibited multifarious morphologies, suggesting that a morphological change of precipitates occurred during long-term service. The M₂₃C₆ carbides and Laves phase coarsened substantially, and the latter grew faster than the former. However, MX carbonitrides exhibited a relatively low coarsening rate. The effect of the evolution of the precipitate phases on the creep rupture strength of P92 steel was discussed.     

CSP热轧板卷边部裂纹成因

用光学显微镜、扫描电镜、透射电镜和能谱分析等方法研究了涟钢CSP热轧板卷边部裂纹的成因.结果表明:连铸坯表面的深振痕是热轧板卷边部裂纹的起源,连铸坯角部过冷导致奥氏体晶界AlN的细小析出,加剧了连铸坯对裂纹的敏感性.连铸坯经过精轧机组的轧制后,连铸坯表面的横裂纹扩展成为热轧板卷的锯齿状裂纹,严重时会造成烂边或掉块.     

均匀化处理温度对6082铝合金组织和性能的影响

采用硬度、电导率测试、金相显微镜、X线衍射、扫描电镜、透射电镜和能谱分析技术,研究均匀化温度对合金组织和性能的影响.研究结果表明:铸态合金由α-Al固溶体和非平衡共晶相组成;490～510℃均匀化,Mg2Si相从过饱和固溶体中析出,在510℃以上均匀化,随着温度的升高,Mg2Si又逐步回溶到基体中,560℃均匀化,Mg2Si相和过剩单质Si完全溶解;随着均匀化温度的升高,非平衡析出物鱼骨状共晶形态逐渐消失,针状β-AlMnFeSi溶解、断裂,转变为具有更高(Mn+Fe)/Si比值颗粒状α-Al(MnFe)Si相,析出相在高温均匀化过程中聚集、球化;560℃均匀化,析出物的连续网状结构转变成链状结构,析出物演化为等轴粒状α-Al(MnFe)Si相.均匀化过程中合金中析出弥散α-Al(MnFe)Si相;在490～560℃保温6h均匀化处理,温度升高,合金的硬度和电导率分别升高和降低.