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solid solution temperature
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  固溶温度
     When solid solution temperature was 530 ℃,deformation amount was 25%,ageing temperature and time separately were 180 ℃ and 2.5 h,mechanical properties were optimal.
     固溶温度为530℃,变形量25%,时效温度180℃,时间2.5h时,薄板的力学性能最好。
短句来源
     By means of microhardness testing and electrical conductivity testing as well as TEM analysis, etc. , the effects of solid solution temperature, aging and cold deforming before aging on microstructure and properties in Cu-0.1%Ag-0.1%Cr alloy were analyzed.
     利用硬度计、导电仪和透射电子显微镜等手段,分析了固溶温度、时效及时效前冷变形量对Cu 0.1%Ag 0.1%Cr合金的组织和性能的影响。
短句来源
     Effect of niobium on ferrous base superalloy with high titanium and medium aluminium was discussed and investigated, the results showed that niobium improved the formation of γ'-phase, increased the amount of γ'phase, formed Ni3(Al、Ti、Nb)and raised the solid solution temperature, with the result that a two-phase strengthening was realized.
     探讨Nb在高Ti中Al铁基高温合金的作用,认为Nb参与了γ'-相形成,增加γ'-相数量,生成Ni3(Al、Ti、Nb)提高γ'-相的固溶温度,从而实现第二相强化。
短句来源
     Effect of Solid Solution Temperature on Structure and Properties of LY11 Aluminium Alloy
     固溶温度对硬铝LY11组织与性能的影响
短句来源
     with rising of heating temperature,recrystallized grain growth demonstrated a trend of increasing:after cold plasticity deformation,when solid solution temperature was within 1 025℃~1 125℃,grain grew slowly;
     再结晶晶粒长大倾向随加热温度的升高表现出增大的趋势:经冷塑性变形后,当固溶温度在1025℃~1125℃时,晶粒缓慢长大;
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  固溶处理温度
     The influence of solid solution temperature on the microstructure and properties of 22Mn-13Cr-5Ni-0. 25N austenitic stainless steel has been investigated.
     研究了固溶处理温度对22Mn-13Cr-5Ni-0.25N奥氏体不锈钢组织和性能的影响。
短句来源
     The formation factors, morphology characteristics of δ ferrite in precipitation hardening stainless steel 17-4PH have been studied. The optimum chemical composition of steel (%): C 0. 030~0. 045, Cr15. 8~16. 4, Ni 4. 10~4. 50, Ti,Al and N no more than 0. 05, and the optimum solid solution temperature1050℃ were obtained.
     研究了17-4PH沉淀硬化不锈钢中δ-铁素体的形成因素、形态特征和化学成分配比,得出最佳成分(%)为:C0.030~0.045,Cr15.8~16.4,Ni4.10~4.50,Ti、Al、N≤0.05,最佳固溶处理温度为1050℃。
短句来源
     the optimal solid solution temperature is 850oC;
     最佳的固溶处理温度为850oC;
短句来源
     The shape memory effect (SME) of Fe-30Mn-6Si-4Cr-5Ni alloy was studied. The influences of solid solution temperature,pre-strain and the recovery annealing temperature on the SME of the alloy were investigated.
     研究了板状Fe-30Mn-6Si-4Cr-5Ni铁基合金的形状记忆效应,探索了固溶处理温度、预应变大小和恢复温度等因素对其形状记忆效应的影响规律。
短句来源
     The results show that the optimal solid solution temperature is 950 ℃, the suitable pre-strain is 5%, and the recovery annealing temperature should not be higher than 400 ℃. 
     结果表明:对于这种螺母,最佳的固溶处理温度为950℃,最适当的预应变为5%,恢复处理温度不超过400℃。
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  “solid solution temperature”译为未确定词的双语例句
     With increasing of solid solution temperature, the strength mechanism evolves from dispersion strength to solid solution strength. And the maximum ductility is obtained at the solid solution temperature of 450K.
     镁锂合金在不同温度下固溶,其基体强化机制随温度升高由弥散强化逐渐转至固溶强化,并在450K左右达到塑性最大值;
短句来源
     The influence of solid solution temperature, pre-strain and recovery annealing temperature on the shape memory effect of FeMnSiCrNi alloy nut component was studied.
     研究了固溶处理工艺、预应变大小和恢复退火温度对FeMnSiCrNi合金螺母形状记忆效应的影响规律。
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The influence of various heat treatments on the microstructure and mechanical properties of 26-5 type ferritic-austenitic stainless steels has been studied from the structural stability viewpoint. It was found that the ratio and morphology of γ-phase in the steel were remarkably influenced by solid solution temperature. It is very important to select an optimum solution temperature range. There are two brittle regions in the specimens having α+γ structure after again at various temperatures...

The influence of various heat treatments on the microstructure and mechanical properties of 26-5 type ferritic-austenitic stainless steels has been studied from the structural stability viewpoint. It was found that the ratio and morphology of γ-phase in the steel were remarkably influenced by solid solution temperature. It is very important to select an optimum solution temperature range. There are two brittle regions in the specimens having α+γ structure after again at various temperatures due to the structural changes caused by the instability of α-ferrite. In order to obtain satisfactory engineering properties for the duplex stainless steels, long period stop at the embrittlement temperature range should be avoided during production and fabrication.

从组织稳定性角度研究了热处理对26-5型铁素体-奥氏体双相不锈钢组织和机械性能的影响。结果指出,不同固溶处理温度对钢中两相比例及作为第二相的奥氏体的形态有显著影响,选择合适的固溶处理制度,对双相不锈钢的性能有决定性意义。固溶处理后,再在较低温度下加热时,由于铁素体相不够稳定而将发生变化,从而在两个温度范围内导致脆化。为了使双相不锈钢具有满意的工程性能,在生产和加工制造过程中,应避免在易产生脆化的温度范围内长时间停留。

The effect of volume fraction and size of fine γ' on creep strength of a directionally solidified nickel-base superalloy——DSK3 at 760℃ has been examined. DSK3 was solution heat treated at 1100—1270℃ to homogenize the alloy and dissolve coarse γ' and eutectic γ—γ' constituents which subsequently reprecipitated in the form of a uniform fine γ' dispersion with various volume fractions (0.25—0.63) and different sizes (0.1—0.3μm) upon cooling and aging. The size and amount of fine γ' increased with the increase of...

The effect of volume fraction and size of fine γ' on creep strength of a directionally solidified nickel-base superalloy——DSK3 at 760℃ has been examined. DSK3 was solution heat treated at 1100—1270℃ to homogenize the alloy and dissolve coarse γ' and eutectic γ—γ' constituents which subsequently reprecipitated in the form of a uniform fine γ' dispersion with various volume fractions (0.25—0.63) and different sizes (0.1—0.3μm) upon cooling and aging. The size and amount of fine γ' increased with the increase of solid solution temperature. The creep rupture life increased and the secondary creep rate decreased as the solution temperature increased and the relationship t_f and e at 760℃ can be expressed as:(?)~αt_f=c where a=1 and c≈5.5. The improvement of creep rupture life was found to be due to a decrease of secondary creep rate and an extension of secondary stage of creep. The secondary creep rate (?) is strongly dependent on size a, interparticle spacing λ and volume fraction v_f of fine γ', and it takes the form:(?)∝α/v_f~(2/3)(1-v_f~(1/3)) or (?)∝λ~2/αThe dislocations structure and morphology of γ' of the alloy produced by creep to primary, secondary and tertiary stage at 760℃ under 73.8 kgf/mm~2 and 78 kgf/mm~2, and at 950℃ under 25 kgf/mm~2 was examined in TEM. During the primary stage of creep at 760℃ under 73.8 kgf/mm~2 or 78 kgf/mm~2 dislocations are moving between the γ' cuboids shearing the γ matrix. Two sets of dislocations intersecting or reacting each other in the γ matrix are visible, but no dislocation is ever observed inside the γ' cuboids. A dense 3-dimensional dislocation network has formed in the γ matrix of the alloy during secondary creep. A few superlattice dislocation pairs were found in the γ' at 760℃ under 78 kgf/mm~2, but still no dislocation in the γ' under 73.8 kgf/mm~2 is observed in secondary stage of creep.The morphology and size of γ' are changing during creep at 950℃ under 25 kgf/mm~2, especially at the end of secondary stage of creep and during tertiary stage of creep. In the early primary stage of creep dislocation structure is similar to that at 760℃ but two sets of α/2<110> dislocations can react more easily and form a 2-dimensional dislocation networks covering the γ—γ' interface in the later primary stage of creep. γ' particles start to coarsen and become a plate shape by lateral merging of cubes without noticeable thickening of the plates from secondary stage of creep.Direct observation of dislocation structure and γ' morphology in relation with secondary creep rate suggests a high temperature creep model for the nickel-base superalloy in the range of temperature and applied stress where shearing of the γ' phase does not control the straining process. During secondary creep, strain is mainly the result of climb rate of dense 2- or 3-dimensional dislocation networks and the free path of dislocation glide in γ. Secondary creep rate (?) can be described as:(?)=NAbR where N is the density of dislocation sources; A the sweeping area of a dislocation, b the magnitude of the Burgers vector of the dislocation and R the climb rate of the dislocation over γ' particle or the number of critical link length of dislocation network can be developed to operate in a unit time, i. e., the number of operating sources of the dislocation in a unit time.The volmne fraction v_f and size of γ' will play an important role in secondary creep rate (?) by changing the configuration and density of the dislocation and influencing the process of the dislocation climb (recovery) in γ matrix. Applying the following equation relating the applied stress and dislocation density ρ to creep process:σ= σ_0+αGbρ~(1/2) where G is the shear modulus, α the strengthening proportional constant by the interaction of dislocations and σ_0 flow stress due to all causes other than dislocation-dislocation interaction, and combining climb model given by Anscll and Weertman the equation for secondary creep rate (?) can be derived as:(?)=K/G~3T λ~2/α(σ-σ_0)~n exp(-Q_s/RT) or (?)=K/G~3T α/v_f~(2/3)(1-v_f~(1/3))~2(σ-σ_0)~n exp (-Q_3/RT) where K is a constant, Q_s the activation energy for self-diffusion, and n=4—5. The expression relating λ, α, v_f and (?) predicted by the theory agrees satisfactorily with experimental results.

本文研究了定向凝固K3镍基高温合金的蠕变强度与细小γ′粒子的数置和尺寸的关系。实验结果证明,随着固溶温度升高,铸态粗大γ′逐步溶解并在随后冷却过程重新析出均匀细小正方形的γ′粒子。细小γ′体积分数(v_f)和尺寸(α)都随固溶温度的升高而增大,当固溶温度从1100℃升至1230℃,v_f从0.25增至0.63,α从0.10μm增至0.32μm。随着固溶温度的升高,第二阶段蠕变速率降低,持久寿命延长,大幅度提高合金的蠕变性能。适当的高温固溶加时效处理(如1210—1230℃,4h+900℃,32h)可提高定向凝固合金的中温(760℃,73.8kgf/mm~2)持久寿命10倍左右。合金的中温蠕变性能取决于细小γ′的体积分数(v_f),尺寸(α)及其间距(λ),在固定温度和应力下,第二阶段蠕变速率((?))与它们之间符合以下关系。 (?)∝λ~2/α或(?)∝α/v_f~(2/3)(1-v_f~(1/3))~2 用透射电镜观察了合金三个蠕变阶段位错亚结构的变化,据此提出蠕变的位错模型和合金的强化机制,并导出第二阶段蠕变速率与γ′体积分数、尺寸和间距之间的关系式,与实验结果完全符合。

One of the chief factors influencing the incipient melting in Hf-bearing DS Ni-base superalloys was found out to be Ni_5Hf-phase. The melting peak at 1135—1160℃ showing Ni_5Hf-phase more than 1.0 v.-% has been determined by DTA on heating. A distinguishable segregation of Ni_5Hf in both ends of the directionally solidified ingots by PD technique was shown, and their sensitivities to incipient melting are quite different consequently, The incipient melting of Ni_5Hf-phase may induce the solution of γ+γ′ eutectic...

One of the chief factors influencing the incipient melting in Hf-bearing DS Ni-base superalloys was found out to be Ni_5Hf-phase. The melting peak at 1135—1160℃ showing Ni_5Hf-phase more than 1.0 v.-% has been determined by DTA on heating. A distinguishable segregation of Ni_5Hf in both ends of the directionally solidified ingots by PD technique was shown, and their sensitivities to incipient melting are quite different consequently, The incipient melting of Ni_5Hf-phase may induce the solution of γ+γ′ eutectic and M_3B_2. It was also obtained that the low-carbon or carbon-free Hf-bearing alloys have stronger tendency to incipient melting, as well as the slow cooling microstructure and the increasing rate of solid solution temperature are sensitive to it. The reduction of rupture strength of the alloys may be caused by the presence of incipient melting of Ni_5Hf more than 3 v.-%. Their rupture is propagated mainly along the interface between the melting zone of Ni_5Hf and the eutectic γ′. By means of pretreatment at 1150℃ for 8h, the Ni_5Hf-phase may be completely eliminated, thus the incipient melting of the Hf-bearing alloys may be effectively brought under control.

含Hf的镍基高温合金存在Ni_5Hf相,它是影响合金初熔的主要因素之一。当该相的量大于1.0v-%时,在加热示差热分析(DTA)曲线上的1135-1160℃处出现Ni_5Hf相的熔化峰。P.D法定向铸锭上、下端存在明显的Ni_5Hf偏析,因而对初熔的敏感性明显不同。Ni_5Hf相的初熔促进了共晶γ′和M_3B_2的熔化。低碳与无碳含Hf合金的初熔倾向更大,缓冷组织和固溶处理的升温速度对初熔是敏感的。高于3V-%的初熔量将会降低合金的持久强度,其断裂主要沿Ni_5Hf初熔区和共晶γ′之间的界面扩展。采用1150℃8h预处理能消除全部的Ni_5Hf相,有效地控制含Hf合金的初熔。

 
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