流体静高压原位磁测量的误差研究（三）——综合兼顾两种影响

 先后选用1至3片非晶Fe_46.3Co_0.03Ni_46.5Si_3.75V_0.92B_2.5合金薄带作样品,插入13层密绕直螺线管内,分别在高静水压容器内和其他四种不同环境中测量它们的磁化曲线、磁导率曲线和起始磁化曲线,再次研究了初级线圈采用多层直螺线管对铁镍合金样品的误差。（１）实验结果表明：既存在样品材料被磁化而形成的退磁场H',也存在漏磁通引起周围铁器磁化而形成的退磁场H'。（２）为了缩小H'的影响,只用1片非晶合金薄带作样品时,H'的影响变得严重,导致μ_m和μ_i出现惊人的误差：Δμ_m/μ_m=50%,Δμ_i/μ_i＝104%。（３）为了综合兼顾这两种影响,采用3片非晶合金薄带作样品时,虽然H'的影响增大一点,但是H'的影响被更多地削弱,所以环境磁化引起的误差反而减小：Δμ_m/μ_m=29%,Δμ_i/μ_i＝15.5%。     

四种非晶磁性合金在流体静高压下的磁化特性

 在0.000 1~2.4 GPa流体静压力范围选30~36个压力点详细测量出FeCoNiSiVB、FeSiB、FeCrSiB和FeCoSiB四种非晶合金磁化曲线和磁导率曲线的压力效应，并采用多项式精确拟合和计算机逐点比较求出四种非晶合金饱和磁感应强度B_s最大磁导率μ_max与压力的关系。发现：（1）总趋势是B_s和μ_max都随压力增加而减小；（2）在2~3各压力区B_s和μ_max皆呈现反常增高。“（1）”可归因于交换积分常数A随原子间距减小而减小，导致磁畴内自发磁化强度下降；“（2）”可能由于在某些窄的压力范围内静水压能够促进非晶合金微结构的短程有序化。     

因瓦合金纳米微粉的恒磁导率及其压力、频率特性和压力相变

 以Fe-30wt%Ni合金片为母合金，用蒸发冷凝法制备了三种粗细不同的纳米微粒。经透射电镜和X光衍射物相分析，微粒成分与母合金一致。5T、5H和3K粉的平均粒度分别为13.6、27和40 mm。在室温和43~28个不同的流体静压力（0.000 1~2.205 GPa）下测量了它们的磁化曲线、磁导率曲线和起始磁化曲线。结果表明：（1）在H＝(20－132)(1000/4π)A/m范围内Fe-30Ni合金三种纳米粉均具有恒磁导率。（2）三种纳米粉恒磁导率随静水压的变化规律如下：μ_r＝3.83+0.253p-0.022 1p²-0.007 22p³（5T粉）；μ_r＝3.93+1.20p-1.97p²+1.52p³-0.510p⁴+0.059 9p⁵（5H粉）；μ_r＝5.96-0.276p+0.107p²-0.045 9p³（3K粉）。前两者随压力增加而升高。后者随压力增加而下降。（3）γ-α马氏体相变明显存在于5T、5H粉中，而3K粉中未见到。（4）Fe-30Ni合金片的μ_i从200kHz至2 MHz已下降一个数量级，而其纳米粉μ_i的频率范围高于300 MHz，增大两个数量级以上。     

非晶铁基合金中两类不同的压磁效应

 本文详细介绍了在0.000 1~2.3 GPa流体静压力下测量三种非晶合金饱和磁感应强度B_s和最大磁导率μ_max的实验方法。实验结果表明：三种非晶合金受压后B_s和μ_max表现各异，可归为两大类。（1）第一类压磁效应：总趋势是B_s和μ_max都随压力增加而下降，但在几个压力区B_s反常增高。如Fe₇₅Ni₅Si₅B₁₅非晶合金B_s随压力增加均匀下降，(Fe_0.85Co_0.15)Cu_0.4Si_4.4B_13.2非晶合金的B_s随压力增加降—升—再降。（2）第二类压磁效应，如Fe_78.75Cu_1.25Si₅B₁₅非晶合金的B_s和μ_max随压力增加都有未见报导过的微弱升高。分别结合局域电子模型的交换作用理论和巡游电子模型的刚带理论进行了讨论。     

坡莫合金纳米粉的恒导磁性及其磁导率的压力、频率特性

 用蒸发冷凝法制备了Fe-50wt%Ni和Fe-84wt%Ni坡莫合金的纳米微粉。经透射电镜X光能谱微区成分分析证实：微粉的成分与原材料的一致；微粉的平均粒径分别为16 nm（Fe-50Ni）和19 nm（Fe-84Ni）。在室温和36个不同的流体静压力（0.000 1~2.205 GPa）下原位测量了它们的磁化和起始磁化曲线。结果表明：（1）Fe-50wt%Ni和Fe-84wt%Ni合金纳米微粉均具有恒导滋特性；（2）这两种纳米粉的起始磁导率随静水压的变化分别为μ_i=8.16+18.2p-24.7p²+18.1p³-6.55p⁴+0.908p⁵（Fe-50Ni合金）和μ_i=5.38-0.169p+0.232p²-0.0786p³（Fe-84Ni合金）；（3）纳米粉的起始磁导率μ_i在频率高于10 MHz才降低，而Fe-50Ni合金片的μ_i在频率高于1 MHz，Fe-84Ni高于100 kHz时就开始下降，故纳米压粉磁芯可应用的频率范围可以比相应组分合金片的大1~2个数量级。     

纳米晶FeCuNbMSiB（M＝Nb，V，Mo）合金的微结构及其电阻率与压力的关系

 X射线衍射和透射电镜的结果表明：非晶FeCuNbMSiB（M＝Nb，V，Mo）合金在540 ℃退火20 min，表面析出的纳米晶是α-FeSi固溶体，粒度为10~20 nm。此外，在0.000 1~2.4 GPa范围内测量了它们的常压室温电阻率以及电阻率随静水压的变化，得到了电阻率与压力的线性关系式。最后探讨了热处理方式和温度对非晶Fe_73.1Cu_1.2Nb_3.2Si_12.5B₁₀合金退火形成纳米晶的影响。     

流体静高压原位磁测量的误差研究──（1）漏磁场的影响

 通过五种不同环境分别做原位磁测量和对比，详细研究了13层密绕直螺线管的漏磁通在同步箍紧式高静水压容器内引起的相对误差（Δc₀/c₀）。结果表明：（1）对于空心次级线圈，Δc₀/c₀为-1.90%～-1.27%（400 Hz）或-0.36%～-0.64%（1 000 Hz）。（2）对于钝铁纳米微粉的（Fe-5H）样品，其磁化曲线及起始磁化曲线均为直线，即具有恒磁导率μ。漏磁通过在高压容器内引起的相对误差，Δμ/μ＝3.9%～3.8%，比（2）约大一倍。     

钨合金的超声测量及力学参量估算

 利用两面顶压机和六面顶压机作为压力装置，分别对93钨合金材料进行了高压超声测量。测得了93钨合金材料在常态下的横、纵波声速及在0~3 GPa压力范围内的纵波声速随压力的变化关系。测量结果为：在常温常压下，93钨合金的纵波声速为c_L＝5.135 km/s，横波声速为c_t＝2.987 km/s。纵波声速随压力变化的关系式为：c_L＝5.053+0.602p（GPa）。估算的93钨合金相关力学参量为：G＝157.4 GPa，E＝393.0 GPa，K＝260.2 GPa，λ＝155.3 GPa，μ＝157.4 GPa，ν＝0.248。经过对两种超声测量方法测量结果的比较及冲击波测量数据的验证，这些参数是可靠的。     

压力对GdoBr:Eu晶场参数的影响

 在室温下测量了GdoBr:Eu的常压和高压荧光谱，光谱范围在13 000~21 500 cm^-1之间，压力至12 GPa。由光谱数据得到了Eu³⁺晶场能级随压力的变化曲线。⁷F_0～5能级随压力的变化规律比较复杂，而⁵D_0~2各能均随压力的升高几乎线性地降低。在基态谱项⁷F的49个状态上进行了晶场拟合计算，所得常压下的5个非零晶场参数分别为：B₀²＝-1 124.0 cm^-1，B₀⁴＝-969.6 cm^-1，B₄⁴＝827.9 cm^-1，B₀⁶＝889.6 cm^-1，B₄⁶＝377.0 cm^-1。高压下的计算结果表明，B₀⁴、B₀⁶这两个晶场参数随压力的增加而增大，B₄⁶随压力的增加而减小，而B₀²、B₄⁴随压力的变化有些起伏。晶场强度在8 GPa以下随压力增加而减小，其后开始变强。     

Cr对Fe-Zr基非晶合金电阻率及压力效应的影响

 在0.000 1~2.5 GPa范围不同静水压下，用四探针法详细测量了七种非晶态Fe_90-xCr_xZr₁₀合金（x=2、4、7、10、13、16、20）的电阻率。结果表明：（1）常压室温电阻率ρ₀与FeZr基非晶合金中Cr含量成N形曲线关系；（2）当静水压增加时，七种非晶合金的约化电阻率（ρ/ρ₀）都单调下降，x越大则电阻率下降的幅度越小；（3）非晶Fe_90-xCr_xZr₁₀合金电阻率的压力系数对x的变化相当敏感；（4）为方便查值，给出了六种典型静水压下ρ/ρ₀与x的曲线关系。最后，讨论了四种物理模型的选用以及相干交换散射在高压下的行为。     

非晶合金条带的爆炸焊接

 报道了利用爆炸焊接技术对铁基、铁镍基非晶合金条带（厚度约25 μm）进行单层和多层爆炸焊接的结果。金相分析结果表明，条带间相互结合良好；X光衍射结果说明，焊接后的条带仍保持非晶态，即使采用表面已有部分晶化德条带进行焊接，焊接后仍转化为非晶态。这说明在焊接过程中条带表面已发生熔化，且冷却速度也可达10⁶ K/s量级。     

Experimental study of regions of reversed magnetization in an amorphous layer of Co70Fe5Si10B15

The characteristics of the distribution of magnetization and remagnetization of microsections of the surface in the amorphous alloy Co₇₀Fe₅Si₁₀B₁₅, prepared in the form of thin ribbons, were studied by the magnetooptical method. It was found that the magnetization I on the surface of the amorphous ribbon studied was strongly nonuniform. It was established that heat treatment (HT) of the sample leads to the appearance of regions of reversed magnetization in the surface layer of the ribbon, while thermomagnetic annealing reduces the nonuniformity of I. The conservation of the transverse component in the HT sample in fields where the magnitude of the component of magnetization parallel to the length of the ribbon remains virtually unchanged suggested that a domain structure of the magnetization ripple type, owing to the strong microdispersion of the magnetic anisotropy, is realized in this sample.Translated from Izvestiya Vysshikh Uchebnykh Zavedenii, Fizika, No. 3, pp. 89–94, March, 1988.     

Magnetic properties of high-Bs Fe–Cu–Si–B nanocrystalline soft magnetic alloys

In the present study, the magnetic properties and microstructures of newly developed Fe–Cu–Si–B alloys prepared by annealing the melt-spun ribbon have been studied. The average size and number density of nanocrystalline grains were about 20 nm and 10²³–10²⁴ m⁻³, respectively. The saturation magnetic flux density B_s for the present alloy is more than 1.8 T, that is about 10% larger than that of Fe-based amorphous alloys. Moreover, core loss P of the present alloy is about half of that of Si-steel up to B=1.7 T.     

具有宽过冷液相区的Fe62Co8-x(Cr,Mo)xNb4Zr6B20非晶态合金的热稳定性与磁性

根据制备块状非晶态合金的三条经验准则,选择了成分为Fe₆₂Co_8-xCr_xNb₄Zr₆B₂₀和Fe₆₂Co_8-xMo_xNb₄Zr₆B₂₀(x=0,2,4)的合金系.利用单辊急冷法制备出厚为30μm宽为5mm左右的条带,并用差热分析、X射线衍射以及 关键词： 过冷液相区 铁磁性 非晶态合金     

Advances in amorphous and nanocrystalline materials

A new amorphous alloy has been recently introduced which shows a saturation magnetic induction B_s of 1.64 T which is compared with B_s=1.57 T for a currently available Fe-based amorphous alloy and decreased magnetic losses. Such a combination is rare but can be explained in terms of induced magnetic anisotropy being reduced by the alloy's chemistry and its heat treatment. It has been found that the region of magnetization rotation in the new alloy is considerably narrowed, resulting in reduced exciting power in the magnetic devices utilizing the material. Efforts to increase B_s also have been made for nanocrystalline alloys. For example, a nanocrystalline alloy having a composition of Fe_80.5Cu_1.5Si₄B₁₄ shows B_s exceeding 1.8 T. The iron loss at 50 Hz and at 1.6 T induction in a toroidal core of this material is 0.46 W/kg which is 2/3 that of a grain-oriented silicon steel. At 20 kHz/0.2 T excitation, the iron loss is about 60% of that in an Fe-based amorphous alloy which is widely used in power electronics. Another example is a Fe₈₅Si₂B₈P₄Cu₁ nanocrystalline alloy with a B_s of 1.8 T, which is reported to exhibit a magnetic core loss of about 0.2 W/kg at 50 Hz and at 1.5 T induction. This article is a review of these new developments and their impacts on energy efficient magnetic devices.     

Magnetic Properties of Amorphous and Nanocrystalline Fe-Zr-B-Al Alloys

We have investigated the influence of aluminium substitution for iron on the magnetic properties of amorphous and nanocrystalline Fe_88-x Zr₇B₅Al _x alloys (x = 0, 1, 3, 5, 7 and 9 at.%). Thermomagnetic curves show an increase of Curie and crystallization temperature of amorphous phase with the increase of the content of aluminium in the alloy. The increase of aluminium content up to 3 at.% Al does not cause the decrease of a saturation magnetization in the as-quenched sample. In addition, magnetostriction of the annealed alloys has been studied. Also, the increase of aluminium content in the alloy causes an increase of the magnetostriction constant.