淬火工艺对Cr26高铬耐磨铸铁组织与硬度的影响

利用光学显微镜、洛氏硬度计等研究了不同淬火工艺对Cr26高铬耐磨铸铁组织与硬度的影响。结果表明:铸态Cr26高铬铸铁组织主要由初生奥氏体和碳化物组成。经980~1060 ℃不同温度淬火、空冷后,高铬铸铁组织中有大量二次碳化物析出。随着淬火温度的升高,析出的二次碳化物先增加后减少,试样硬度先升高后降低。1020 ℃淬火试样硬度达到峰值,为65.7 HRC。1020 ℃淬火高铬铸铁,经空淬、油淬和水淬不同方式冷却,随着冷却速度的增大,高铬铸铁组织中碳化物颗粒、碳化物比例逐渐增大,硬度逐渐增大,其中水淬高铬铸铁试样硬度最大,达到68.2 HRC。     

基于末端淬火试验2124铝合金的淬透性

通过Jominy末端淬火实验研究2124铝合金的淬透性。利用温度数据采集、布氏硬度检测、差示量热法(DSC)和透射电子显微镜(TEM)等手段分析淬火冷却速率对时效后第二相析出行为的影响。结果表明:Jominy末端淬火2124铝合金室温水淬硬度下降小于10%的淬透深度大约为50 mm,该位置处合金在222.7～350.0℃温度区间的平均淬火冷却速率大于2.0℃/s;较低的淬火冷却速率致使过饱和的溶质原子和空位损失,导致时效析出相变驱动力不足,显著削弱了时效强化效果。     

固溶处理对铝合金7050-T6淬透层深度的影响

采用末端淬火试验和OM、SEM、EDS、XRD和TEM方法研究了不同温度固溶处理对7050铝合金材料淬透层深度的影响.结果表明,影响7050铝合金淬透层深度的特征微结构因素是随淬火冷却速度降低析出的η平衡相尺寸和体积分数.475 ℃保温固溶(S475)试样中还存在较多的粗大Al2CuMg(S)相,490 ℃保温固溶(S490)试样中S相几乎全部溶入基体,淬火后能形成更高的合金原子浓度,有利于时效处理时形成数量更多、密度更大的强化相,在同等淬火条件下,S490-T6的淬透层深度比S475-T6增加约36%.     

7050铝合金热轧板的淬火敏感性

用末端淬火、光学金相显微镜和透射电镜技术研究7050铝合金热轧板的淬火敏感性.结果表明:7050铝合金端淬火试样硬度下降10%的淬透深度约60mm.决定7050铝合金淬火敏感性的本质是析出的η平衡相的尺寸和体积分数,主要发生η相析出的淬火临界平均冷却速率约为40℃/s,此时η相的体积分数约为2.1%.淬火平均冷却速率低于40℃/s,η相析出和粗化一再结晶-Al3Zr非共格化交互影响.     

7B50铝合金淬透性及其临界平均冷却速率的研究

本研究通过7B50合金改进型Jominy样品表面喷水淬火实验,在获得实测冷却曲线、不同时效状态合金的电导率和硬度的基础上,结合自然时效状态合金的微观组织,对7B50合金的淬透性及其临界平均冷却速率展开研究。结果表明:7B50合金自然时效50 d的淬透深度为70 mm,对应淬火敏感温度区间(420～230℃)内的平均冷却速率为1.55℃×s~(-1);先自然时效50 d再人工峰时效合金的淬透深度减至60 mm,对应的平均冷却速率为1.95℃×s~(-1);与自然时效状态相比,先自然时效再人工峰时效处理后合金的淬透性变差,淬火敏感性增加。表面喷水淬火时,非均匀析出相首先在晶界/亚晶界上析出,然后在基体内的Al_3Zr粒子上析出;晶界/亚晶界上观察到析出相,出现在距淬火表面仅3mm处,对应淬火敏感温度区间内的平均冷却速率高达981℃×s~(-1);基体内零星析出尺寸较小的非均匀析出相,出现在距淬火表面10mm处,对应的平均冷却速率为37.75℃×s~(-1)。喷水淬火后,距淬火表面25 mm处的性能与淬火表面处相比变化不大,该位置对应的平均冷却速率为9.34℃×s~(-1),远小于淬火表面处,控制7B50合金厚板的喷水淬火过程,使厚板内部的平均冷却速率接近但不低于9.34℃×s~(-1),厚板淬火-时效后将获得较好的性能。     

7075铝合金的淬火敏感性(英文)

7075铝合金广泛用于要求高力学性能的零部件。有关技术文献指出,该合金的耐蚀性和力学性能主要决定于淬火冷却速度。这种现象通常称为"淬火敏感性"。本文的主要目的是,通过改变热处理工艺参数和轧制方向(L,LT,ST)来研究板材试样的淬火冷却速度对其性能的影响。试样均在实验室设备中热处理,以获得T6、T76和T73处理状态。试样为长方体(13 mm 13 mm 100 mm),水淬,通过改变水温或改变温度为20℃、用水搅动的浴槽中聚合物浓度来调节淬火冷却速度。在每种实验条件下,均采用置于试样中的热电偶测量冷却速度。此外,还进行了有限元(FEM)模拟试验,以测定所有试验条件下冷却过程的热传递系数;进行了拉伸试验和晶间腐蚀试验,以弄清所研究的冷却速度对7075合金板材性能的影响。     

淬火对汽车车身用6022铝合金烤漆硬化效应的影响

以6022铝合金冷轧板为研究对象,通过显微组织观察、硬度测试等方法研究了双级淬火工艺对6022铝合金组织及烤漆前后硬度的影响。结果表明:6022铝合金试样经过560℃×25 min固溶处理后,进行油淬+室温水淬双级淬火,油淬温度越高,6022铝合金硬度越高,对抑制自然停放效应不利影响的作用越明显。6022铝合金最佳的双级淬火工艺为110℃×50 min油淬+室温水淬。此淬火工艺下的试样烤漆前硬度为71 HV,利于冲压成形,烤漆后,硬度值达到108 HV,烤漆硬化效应值为37 HV,烤漆硬化效应明显。     

1Cr13Ni马氏体钢不同冷却方式的回火组织与力学性能研究

对经过不同冷却方式冷却后的1Cr13Ni马氏体钢进行回火处理,研究了1Cr13Ni马氏体钢冷却速度对后续回火处理材料的组织与力学性能影响规律。结果表明:水淬、油淬、空冷时的回火组织主要是索氏体、铁素体以及析出的碳化物。炉冷时的回火组织主要是铁素体和珠光体,以及沿晶界区域析出的大量碳化物。冷却速度越快,马氏体相变程度越大,回火组织的硬度与抗拉强度相应增加,最大抗拉强度为1191 MPa。560℃回火后各试样的硬度、抗拉强度、断面收缩率随着淬火冷却速度的增大而增大,伸长率随着冷却速度的增加而减小。炉冷试样晶界区域有大面积珠光体组织形成,回火后强度与硬度最小。     

钢的U曲线数学模型

建立了描述淬火钢圆形截面硬度分布曲线——U曲线的解析函数表达式．首先求得端淬试样冷至700℃时的冷却速率计算公式．根据端淬曲线、冷却速率和圆截面半径关系实验曲线图及等效冷速原理,用曲线拟合法获得了硬度与试样半径和截面上所处位置半径之间关系式．截面硬度分布函数含有从端淬实验曲线获得的淬透性系数、最高硬度和最低硬度值,使得模型具有较高的合理性且保证了淬透性系数与试样形状无关．实验验证结果表明,根据本文模型模拟所得结果与实验测试值符合很好．     

高频淬火缺陷分析

齿轮和轴类零件采用高频淬火处理来改善表面组织结构,提高表面硬度和强度,以提高零件的使用寿命。高频淬火时,若工艺和操作不当,使零件产生裂纹等缺陷,造成废品。 (1)淬硬层深度达不到技术要求:高频淬火淬硬层深度一般为0.5—2mm,但有时小于0.5mm。对于选定材科,影响淬透深度的因素是电流频率和工件旋转、移动速度。因此,为了达到一定的淬硬层深度,需选择合适的电流频率和工件旋转、移动速度。 (2)软点与软带:软点为淬火件个别区域的硬度比邻近区域的硬度低得多。其主要是由于冷却液不纯净、含有油珠,使局部冷却速度降低(小于临界冷却速度),或工件局部氧化     

Characterization of γ′ precipitates in a nickel base superalloy quenching from aging temperature at different rates

The characteristics of γ′ precipitates in a superalloy quenched from 1050°C at different rates were investigated using field emission scanning electron microscope(FESEM).When quenched from 1050°C, the size of primary aging γ′ precipitates has a small increase in the specimens that experienced iced-brine-quenching, oil-quenching, and air-cooling-quenching conditions and a drastic increase in the specimen that experienced a furnace-cooling-quenching condition.The cooling γ′ precipitates have unimodal distributions after quenching at the air-cooling rate and bimodal distributions after quenching at the furnace-cooling rate, but there are not these distributions in the specimens that experienced iced-brine-quenching and oil-quenching conditions.When aging at 760°C, the size of primary aging γ′ precipitates appears unaffected in the specimens that experienced iced-brine-quenching, oil-quenching, and air-cooling-quenching conditions.However, it has a drastic increase in the specimen that experienced a furnace-cooling-quenching condition, and it is interesting that the bigger cooling γ′ precipitates have a coalescence and octodendritic shape.The microhardness study indicates that the hardness has no variation in the specimens that experienced iced-brine-quenching, oil-quenching, and air-cooling-quenching conditions and has a drastic decrease in the specimens that experienced a furnace-cooling-quenching condition and obtains the minimum microhardness value 390.8 HV.     

Optimization of conductivity and strength in Cu-Ni-Si alloys by suppressing discontinuous precipitation

Cu-Ni-Si alloys with and without Ti were solution treated at 980 °C for 1 h and cooled by air cooling and water quenching, after which the specimens were aged at 500 °C. The two alloys showed different aging characteristics with different cooling rates during the aging process. The conductivity of all alloys increased during aging; for alloys that were water quenched, hardness increased at the early stage of aging and then drastically decreased. The air-cooled Cu-Ni-Si alloy without Ti also experienced an increase in hardness, which then decreased during aging, but the air-cooled Cu-Ni-Si alloy with Ti did not show a drastic decrease in hardness during prolonged aging. A combination of yield strength and conductivity of 820 MPa and 42% IACS, respectively, was achieved in the air-cooled Cu-Ni-Si-Ti alloy after solution treatment.     

Effect of cold deformation and heat treatment on microstructure and mechanical properties of TC21 Ti alloy

In the present research work on TC21 titanium alloy (6.5Al−3Mo−1.9Nb−2.2Sn−2.2Zr−1.5Cr), the effects of cold deformation, solution treatment with different cooling rates and then aging on microstructure, hardness and wear property were investigated. A cold deformation at room temperature with 15% reduction in height was applied on annealed samples. The samples were solution-treated at 920 °C for 15 min followed by different cooling rates of water quenching (WQ), air cooling (AC) and furnace cooling (FC) to room temperature. Finally, the samples were aged at 590 °C for 4 h. Secondary α-platelets precipitated in residual β-phase in the case of solution-treated samples with AC condition and aged ones. The maximum hardness of HV 470 was obtained for WQ + aging condition due to the presence of high amount of residual β-matrix (69%), while the minimum hardness of HV 328 was reported for FC condition. Aging process after solution treatment can considerably enhance the wear property and this enhancement can reach up to about 122% by applying aging after WQ compared with the annealed samples.     

Effects of Isothermal Aging on Microstructure Evolution,Hardness and Wear Properties of Wrought Co-Cr-Mo Alloy

In this work, effects of isothermal aging on phase transformation, microstructure evolution, hardness and wear resistance of the wrought Co-Cr-Mo alloy with low carbon content were investigated. Initially, temperature range of FCC to HCP phase transformation of the alloy was determined by a dilatometer test. Then, aging at the temperature of 850 °C for different holding times with subsequent water quenching was carried out. Metallography examination, x-ray diffraction analysis, microhardness test and wear test were performed for Co-Cr-Mo alloy specimens after the isothermal aging. It was found that the FCC to HCP phase transformation occurred in the temperature range between 700 and 970 °C. During the aging treatment, phase fraction of the HCP martensite increased with longer aging time. The FCC to HCP phase transformation was completed after 12 h, because very fine lamellae in different orientations thoroughly dispersed within FCC grains were observed. These lamella structures could be well correlated with formation of the HCP martensite. Small amounts of carbides were found at grain boundaries and grain intersections in the samples aged for 6 and 12 h. In addition, by longer aging time, the average grain size of the aged alloy became a little bit larger, while the hardness noticeably increased. For the examined Co-Cr-Mo alloy, higher amount of the emerged HCP martensitic phase led to the increased hardness value, but reduced friction coefficient and wear rate.     

Microstructural and Hardness Studies of Cu-10wt.%Sn Alloy Under Different Aging Conditions

Microstructure of Cu-10wt.%Sn alloy, prepared by powder metallurgy technique and sintered at 900 °C for 120 min in hydrogen atmosphere, was studied by optical microscopy and XRD technique as a function of aging time. Isothermal aging of the alloy specimens was performed at 250 °C for a period of 30, 60, 120, 300, and 1440 min after solution treatment at 500 °C for 60 min. Rockwell hardness of aged specimens was also measured at room temperature as a function of aging time. It was observed that microstructure of the as-sintered specimens consists of the grains of alpha Cu-Sn solid solution. Moreover, solution treatment of the alloy specimens followed by quenching in water increased the hardness of the as-sintered alloy specimens from 35.5 to 59.8 HRF due to the residual stresses generated by fast cooling. Aging at 250 °C for 30, 60, and 120 min was found to cause a decrease in hardness from 59.8 to 45.1 HRF, whereas the specimens aged for 300 and 1440 min show an increase in hardness from 45.1 to 75.7 HRF. The values of porosity calculated from XRD patterns of the alloy specimens referred to show that porosity varies with aging time in a manner opposite to that of hardness, e.g., porosity is maximum for 120 min aging time where hardness is minimum.     

Effect of precipitation from tweed matrix on the mechanical properties in a metastable beta alloy of Ti-15-3

The effects of aging treatment on the microstructures and mechanical properties of a metastable beta titanium alloy Ti-15-3 (Ti−15V−3Al−3Sn-3Cr) have been investigated with hardness measurements, tensile test, and optical and electron microscopy. Precipitate-free beta structure with average grain size of about 56 μm was obtained after solution treatment at 800°C for 15 min followed by air cooling. Solution treated specimens were aged up to 800 h in the temperature range between 350 and 600°C. The morphology of the precipitates was varied significantly, depending on the aging temperature. The fine aggregates of α precipitates were dominant above 450°C. Peak hardness values were maintained up to 800 h at 500°C, which showed the superior thermal stability of α precipitates. Tensile strength increased up to 1600 MPa along with the decrease of elongation after aging at 350 and 400°C.     

Computation of synthetic surface heat transfer coefficient of 7B50 ultra-high-strength aluminum alloy during spray quenching

According to inverse heat transfer theory, the evolutions of synthetic surface heat transfer coefficient (SSHTC) of the quenching surface of 7B50 alloy during water-spray quenching were simulated by the ProCAST software based on accurate cooling curves measured by the modified Jominy specimen and temperature-dependent thermo-physical properties of 7B50 alloy calculated using the JMatPro software. Results show that the average cooling rate at 6 mm from the quenching surface and 420–230 °C (quench sensitive temperature range) is 45.78 °C/s. The peak-value of the SSHTC is 69 kW/(m²·K) obtained at spray quenching for 0.4 s and the corresponding temperature of the quenching surface is 160 °C. In the initial stage of spray quenching, the phenomenon called “temperature plateau” appears on the cooling curve of the quenching surface. The temperature range of this plateau is 160–170 °C with the duration about 3 s. During the temperature plateau, heat transfer mechanism of the quenching surface transforms from nucleate boiling regime to single-phase convective regime.     

Study on inhomogeneous cooling behavior of extruded profile with unequal and large thicknesses during quenching using thermo-mechanical coupling model

The interfacial heat transfer coefficient between hot profile surface and cooling water was determined by using inverse heat conduction model combined with end quenching experiment. Then, a Deform-3D thermo-mechanical coupling model for simulating the on-line water quenching of extruded profile with unequal and large thicknesses was developed. The temperature field, residual stress field and distortion of profile during quenching were investigated systematically. The results show that heat transfer coefficient increases as water flow rate increases. The peak heat transfer coefficient with higher water flow rates appears at lower interface temperatures. The temperature distribution across the cross-section of profile during quenching is severe nonuniform and the maximum temperature difference is 300 °C at quenching time of 3.49 s. The temperature difference through the thickness of different parts of profile first increases sharply to a maximum value, and then gradually decreases. The temperature gradient increases obviously with the increase of thickness of parts. After quenching, there exist large residual stresses on the inner side of joints of profile and the two ends of part with thickness of 10 mm. The profile presents a twisting-type distortion across the cross-section under non-uniform cooling and the maximum twisting angle during quenching is 2.78°.     

对自来水作为淬火介质的两大缺点的研究

从自来水淬火时工件容易淬裂、硬度不均且畸变大等现象，列出了自来水作为淬火介质的两大缺点：一是低温冷却速度太快，二是冷却特性对水温变化太敏感。分析了自来水第二大缺点引起淬火硬度不均和畸变的原因。通过与气态介质的对比，指出了液态淬火介质共同的两类缺点：一是任何确定的液态介质，其冷却速度的可调节范围都很有限，以致同一个车间必须配备普通淬火油、中速淬火油和高速淬火油，才能满足不同工件的需要；二是工件从蒸汽膜阶段到沸腾阶段期间，冷却速度突然增大，可能引起较大的淬火畸变。提供了克服液态淬火介质第二类缺点的七类技术方法。     

Effect of hardening conditions on mechanical properties of high speed steels

Abstract

Hardness and toughness are the main properties determining wear resistance and performance of high speed steel tools. The objective of the present paper was to study the effect of hardening conditions on the toughness of high speed steels, mainly concerning the hardening temperature and cooling rate during quenching. Several conditions were simulated in laboratory and industrial heat treatment furnaces and toughness was evaluated through the static bend test. Under the same tempering condition, the higher the hardening temperature, the higher the attained hardness. The results also point out a compromise situation between hardness and toughness, until 1200°C hardening temperature is reached; for temperatures over this value, the loss in toughness become more accentuated, without a considerable increase in hardness. The present paper also describes the mechanical properties of M2 high speed steel heat treated to lower hardness, necessary in some cold work tooling applications. In this case, hardening at lower temperatures and tempering close to the peak hardness has shown the best results. And lastly, regarding cooling conditions during nitrogen hardening in a vacuum furnace, the results point out that low quenching pressures might reduce the cooling rate and decreases material toughness, but the differences are very small for pressures between 6 and 9 bar.