**3.1. Thermal decomposition of organometallic precursor**

Figure 2 shows the TG-DTA curves of the organometallic precursor obtained by the hot soap method. In the TG curve, there are four temperature regions based on weight loss: (1) RT ~ 220°C, (2) 220 ~ 420°C, (3) 420 ~ 510°C, and (4) 510 ~ 600°C, in which the corresponding organic weight loss of 4%, 38%, 45% and 1% were observed, respectively. The small weight loss of the region (1) was ascribed to the evaporation of residual water and ethanol. While the large weight loss of the region (2), accompanied with faint endo- or exothermal peaks in the DTA curve, corresponded to the sublimation and the decomposition of excessive organic substances such as PEG, oleic acid and oleylamine. The temperature range of the region (2) was coincident with the boiling points of individual substances of 250°C (PEG), 223°C (oleic acid) and 350°C (oleylamine). The region (3) comprised the combustion reaction of the residual organics and carbonate components as suggested by the large exothermal peaks at 460°C and 500°C. The large weight loss was due to the decomposition of the most of the organics by oxidation and the release of NOx, H2O, CO and CO2 gases, together with the formation of LaFeO3 as discussed latter. Further heat-treatment in the region (4) gave no major weight loss anymore.

**Figure 2.** TG-DAT curves of the precursor. The solid triangles indicate the set temperatures for the subsequent XRD and IR observations.

In order to identify the structural changes of the resultant precursor after the heattreatment, we measured XRD and IR spectra of heat-treated samples taken out from the TG-DTA furnace immediately after reaching to the set temperatures. Figure 3 shows the XRD patterns of the heat-treated samples at various set temperature by TG-DTA. The XRD pattern of the precursor powder had no sharp diffraction lines resulting from the formation of perovskite type oxides. The broad bands centered at around 2 = 30° and 45° suggested the existence of disordered La2O3 phase [21]. Scarce changes in XRD patterns were observed up to the heating of 450 °C. However the XRD pattern of the specimen heated at 550 °C showed clear peaks attributed to LaFeO3 perovskite phase. The pattern showed only the presence of the orthorhombic LaFeO3 phase without the broad bands. Observed crystallization temperature between 450 and 550°C was very consistent with the thermal decomposition temperature of the precursor associated with the large exothermal peaks on the corresponding TG-DTA curves (Figure 2).

major weight loss anymore.

subsequent XRD and IR observations.

the corresponding TG-DTA curves (Figure 2).

the large weight loss of the region (2), accompanied with faint endo- or exothermal peaks in the DTA curve, corresponded to the sublimation and the decomposition of excessive organic substances such as PEG, oleic acid and oleylamine. The temperature range of the region (2) was coincident with the boiling points of individual substances of 250°C (PEG), 223°C (oleic acid) and 350°C (oleylamine). The region (3) comprised the combustion reaction of the residual organics and carbonate components as suggested by the large exothermal peaks at 460°C and 500°C. The large weight loss was due to the decomposition of the most of the organics by oxidation and the release of NOx, H2O, CO and CO2 gases, together with the formation of LaFeO3 as discussed latter. Further heat-treatment in the region (4) gave no

**Figure 2.** TG-DAT curves of the precursor. The solid triangles indicate the set temperatures for the

In order to identify the structural changes of the resultant precursor after the heattreatment, we measured XRD and IR spectra of heat-treated samples taken out from the TG-DTA furnace immediately after reaching to the set temperatures. Figure 3 shows the XRD patterns of the heat-treated samples at various set temperature by TG-DTA. The XRD pattern of the precursor powder had no sharp diffraction lines resulting from the formation of perovskite type oxides. The broad bands centered at around 2 = 30° and 45° suggested the existence of disordered La2O3 phase [21]. Scarce changes in XRD patterns were observed up to the heating of 450 °C. However the XRD pattern of the specimen heated at 550 °C showed clear peaks attributed to LaFeO3 perovskite phase. The pattern showed only the presence of the orthorhombic LaFeO3 phase without the broad bands. Observed crystallization temperature between 450 and 550°C was very consistent with the thermal decomposition temperature of the precursor associated with the large exothermal peaks on

**Figure 3.** Typical XRD patterns of the obtained products heat-treated at various set temperatures in TG-DTA furnace with no holding time.

**Figure 4.** Corresponding IR spectra of the obtained products shown in Figure 3.

The crystallization of LaFeO3 was fully accompanied with the decomposition of the organic substances. The corresponding IR spectra of the heat-treated samples at various set temperatures of TG-DTA are shown in Figure 4. The IR spectra clearly provided the evidence for the presence of organic substances in the precursor. The strong absorption bands at about 2900 cm-1 were assigned to the olefinic C-H stretching bands. While the bands appearing at 1400 ~ 1600 cm-1 were characteristics of the metal chelate compounds with carbonyl groups [22, 23]. Two strong peaks at 1550 and 1450 cm-1 were mainly assigned to the C=O asymmetric and symmetric stretching modes, respectively. The metal ions in the precipitate could be coordinated with large amount of organic molecules and the large weight loss (87%) at 500°C was confirmed after the thermal decomposition. With increasing the heat-treated temperature, the absorption bands assigned to the organic bonds were gradually decreased in intensity and nearly vanished at 550°C. Besides the strong new band appeared at 600 cm-1, that can be attributed to the Fe-O stretching vibration band due to the formation of LaFeO3 phase [24]. These results fully agreed with the XRD phase-analysis findings.

#### **3.2. Formation of LaFeO3 nanoparticles**

As shown in Figure 2 in the previous section, a large weight loss of the precipitate started at 220°C, much lower than the temperature of the combustion of the residual organics and the crystallization of LaFeO3. Moderate decomposition of organic substances in the precursor seemed to start prior to the combustion. The migration of metal ions should be facilitated even at the lower temperature. Therefore the long time heat-treatments below the combustion temperature were conducted to the precursors to prepare nanocrystalline particles. Figure 5 shows the XRD patterns of the samples heat-treated in air for 6 h at various temperatures below the combustion. The sample heated at 325°C showed the diffuse XRD pattern with no crystalline phases. While at 350°C, broad XRD peaks attributed to the LaFeO3 perovskite phase started to be observed. This temperature was much lower than the crystallization temperature deduced by the TG-DTA curves. The average grain size, t, of LaFeO3 particles estimated from the XRD peak broadening for the LaFeO3(121) lines was summarized in Table 1 by using the Scherrer equation: t = ��� �����, where λ is the x-ray wavelength, B is the line broadening at half the maximum intensity (FWHM) in radians, and θ is the Bragg angle. The particle size of LaFeO3 formed at 350°C was about 16 nm. With increasing the heat-treatment temperature, the XRD peaks became sharper because of the grain growth of the LaFeO3 particles.


**Table 1.** Average crystallite size of LaFeO3 nanoparticles as a function of the heat- treatment temperature.

The crystallization of LaFeO3 was fully accompanied with the decomposition of the organic substances. The corresponding IR spectra of the heat-treated samples at various set temperatures of TG-DTA are shown in Figure 4. The IR spectra clearly provided the evidence for the presence of organic substances in the precursor. The strong absorption bands at about 2900 cm-1 were assigned to the olefinic C-H stretching bands. While the bands appearing at 1400 ~ 1600 cm-1 were characteristics of the metal chelate compounds with carbonyl groups [22, 23]. Two strong peaks at 1550 and 1450 cm-1 were mainly assigned to the C=O asymmetric and symmetric stretching modes, respectively. The metal ions in the precipitate could be coordinated with large amount of organic molecules and the large weight loss (87%) at 500°C was confirmed after the thermal decomposition. With increasing the heat-treated temperature, the absorption bands assigned to the organic bonds were gradually decreased in intensity and nearly vanished at 550°C. Besides the strong new band appeared at 600 cm-1, that can be attributed to the Fe-O stretching vibration band due to the formation of LaFeO3

As shown in Figure 2 in the previous section, a large weight loss of the precipitate started at 220°C, much lower than the temperature of the combustion of the residual organics and the crystallization of LaFeO3. Moderate decomposition of organic substances in the precursor seemed to start prior to the combustion. The migration of metal ions should be facilitated even at the lower temperature. Therefore the long time heat-treatments below the combustion temperature were conducted to the precursors to prepare nanocrystalline particles. Figure 5 shows the XRD patterns of the samples heat-treated in air for 6 h at various temperatures below the combustion. The sample heated at 325°C showed the diffuse XRD pattern with no crystalline phases. While at 350°C, broad XRD peaks attributed to the LaFeO3 perovskite phase started to be observed. This temperature was much lower than the crystallization temperature deduced by the TG-DTA curves. The average grain size, t, of LaFeO3 particles estimated from the XRD peak broadening for the LaFeO3(121) lines

wavelength, B is the line broadening at half the maximum intensity (FWHM) in radians, and θ is the Bragg angle. The particle size of LaFeO3 formed at 350°C was about 16 nm. With increasing the heat-treatment temperature, the XRD peaks became sharper because of the

> 350 16 450 20 500 22

**Table 1.** Average crystallite size of LaFeO3 nanoparticles as a function of the heat- treatment

Crystallite size (nm)

�����, where λ is the x-ray

phase [24]. These results fully agreed with the XRD phase-analysis findings.

was summarized in Table 1 by using the Scherrer equation: t = ���

Heat-treatment temperature (°C)

**3.2. Formation of LaFeO3 nanoparticles** 

grain growth of the LaFeO3 particles.

temperature.

**Figure 5.** Typical XRD patterns of the obtained products after the long time heat-treatment (6 h) at various temperatures.

**Figure 6.** IR spectra of the obtained products after the long time heat-treatment (6 h) shown in Figure 5.

Decomposition of organic substances after the heat-treatment below the combustion temperature was examined by IR spectroscopy. Figure 6 shows the IR spectra of long time (6h) heat-treated samples at various temperatures. The precursor should consist of organometallic composites derived from starting materials. The IR spectrum indicated the clear bands assigned to C-H stretching (~2900 cm-1) and C-O stretching (1400~1600 cm-1) of organic substances [22, 23]. With increasing the heat-treatment temperature, the intensities of initial bands steeply decreased and a new band assigned to Fe-O stretching (~600 cm-1) started to appear at 325°C. This temperature was slightly lower than the formation temperature of LaFeO3 nanoparticles confirmed by XRD observations. And the Fe-O stretching band was intensified monotonically with increasing the temperature. By the way, subsequent to diminishing the intensity of olefinic C-H stretching bands, new strong band appeared in the spectra at 1475 cm-1 in addition to a weak band at 843 cm-1. The former band could be assigned to aromatic C=C stretching vibration, while the latter was to aromatic C– H bending one [25]. This result suggested that the framework of organic matrix in precursor was considerably changed after the long time heat-treatment below the combustion temperature. The heat-treatment seemed to promote carbonization of organic substances as well as the crystallization of LaFeO3 nanoparticles.

SEM images of the obtained powders heat-treated in air at various temperatures for 6 h are shown in Figure 7. The precursor particles with and without heat-treatment at 325°C revealed the smooth surface with squamous and wrinkled structures, respectively. These surface morphologies should be very consistent with the amorphous nature of the resultant organic matrix. With increasing the heat-treatment temperature above 350°C, the particles were crowned by squamous surfaces. The macrosized particles seemed to be disaggregated into fine particles after the crystallization. In spite of the nanometric crystal size determined from the XRD profiles, the BET surface area of the obtained LaFeO3 particles at 350 and 500°C were only 3.9 and 3.1 m2/g, respectively. The nanocrystalline fine particles formed in the precursors were strongly agglomerated with each other in present cases. The residual carbon matrix could also affect the morphology of the obtained powders.

The structure of the LaFeO3 nanocrystallites was further analyzed by TEM micrograph. Figure 8 shows the TEM image and electron diffraction (ED) pattern of LaFeO3 nanoparticles obtained by the long time (6 h) heat-treatment at 350°C. The particulates consisted of an agglomeration of numerous spherical primary particles loosely aggregated together, in contrast to the SEM observations. The average diameter of the primary particles estimated from the TEM image was about 15 nm, which was well consistent with that from XRD. The high-contract dotted rings in the ED patterns indicated the good crystallinity of the LaFeO3 nanoparticles. These rings were indexed as the LaFeO3 perovskite phase with random orientation. No diffraction spots attributed to the secondary phase were observed.

#### **3.3. Magnetic properties of LaFeO3 nanoparticles**

Room temperature Mössbauer spectra of obtained powders after the long time heattreatment (6h) at various temperatures are shown in Figure 9. The sample heated at 500°C, which had a larger crystallite size, showed a clear sextet pattern with a small amount of a

well as the crystallization of LaFeO3 nanoparticles.

Decomposition of organic substances after the heat-treatment below the combustion temperature was examined by IR spectroscopy. Figure 6 shows the IR spectra of long time (6h) heat-treated samples at various temperatures. The precursor should consist of organometallic composites derived from starting materials. The IR spectrum indicated the clear bands assigned to C-H stretching (~2900 cm-1) and C-O stretching (1400~1600 cm-1) of organic substances [22, 23]. With increasing the heat-treatment temperature, the intensities of initial bands steeply decreased and a new band assigned to Fe-O stretching (~600 cm-1) started to appear at 325°C. This temperature was slightly lower than the formation temperature of LaFeO3 nanoparticles confirmed by XRD observations. And the Fe-O stretching band was intensified monotonically with increasing the temperature. By the way, subsequent to diminishing the intensity of olefinic C-H stretching bands, new strong band appeared in the spectra at 1475 cm-1 in addition to a weak band at 843 cm-1. The former band could be assigned to aromatic C=C stretching vibration, while the latter was to aromatic C– H bending one [25]. This result suggested that the framework of organic matrix in precursor was considerably changed after the long time heat-treatment below the combustion temperature. The heat-treatment seemed to promote carbonization of organic substances as

SEM images of the obtained powders heat-treated in air at various temperatures for 6 h are shown in Figure 7. The precursor particles with and without heat-treatment at 325°C revealed the smooth surface with squamous and wrinkled structures, respectively. These surface morphologies should be very consistent with the amorphous nature of the resultant organic matrix. With increasing the heat-treatment temperature above 350°C, the particles were crowned by squamous surfaces. The macrosized particles seemed to be disaggregated into fine particles after the crystallization. In spite of the nanometric crystal size determined from the XRD profiles, the BET surface area of the obtained LaFeO3 particles at 350 and 500°C were only 3.9 and 3.1 m2/g, respectively. The nanocrystalline fine particles formed in the precursors were strongly agglomerated with each other in present cases. The residual

The structure of the LaFeO3 nanocrystallites was further analyzed by TEM micrograph. Figure 8 shows the TEM image and electron diffraction (ED) pattern of LaFeO3 nanoparticles obtained by the long time (6 h) heat-treatment at 350°C. The particulates consisted of an agglomeration of numerous spherical primary particles loosely aggregated together, in contrast to the SEM observations. The average diameter of the primary particles estimated from the TEM image was about 15 nm, which was well consistent with that from XRD. The high-contract dotted rings in the ED patterns indicated the good crystallinity of the LaFeO3 nanoparticles. These rings were indexed as the LaFeO3 perovskite phase with random

orientation. No diffraction spots attributed to the secondary phase were observed.

Room temperature Mössbauer spectra of obtained powders after the long time heattreatment (6h) at various temperatures are shown in Figure 9. The sample heated at 500°C, which had a larger crystallite size, showed a clear sextet pattern with a small amount of a

**3.3. Magnetic properties of LaFeO3 nanoparticles** 

carbon matrix could also affect the morphology of the obtained powders.

**Figure 7.** SEM images of the obtained products heat-treated at various temperatures.

doublet component. The observed Mössbauer parameters showing antiferromagnetic ordering were fully consistent with those of the LaFeO3 bulk crystals [26]. The paramagnetic doublet patterns were dominant for other samples obtained at lower temperatures (350 and 450°C) in spite of the formation of LaFeO3, as well as the non-crystalline samples at 300 and 325°C. This behavior was attributed to superparamagnetism because of the fine crystallite size of LaFeO3 as discussed above. By the way, the doublet patterns showed asymmetric profiles. The asymmetric doublets were probably caused by the presence of iron ions in different environments such as surface or inner part of the crystals and/or the noncrystalline matrix. But it was difficult to decompose such complex spectra into unique components. Therefore the spectra were simply analyzed to assume one asymmetric doublet with different widths. The fitted parameters are listed in Table 2. The isomer shift values of ~0.3 mm/s for both doublet and sextet peaks indicated the Fe valence states in the all specimens were trivalent. No reduction occurred during the long time heat-treatment with organic substances. When looking in detail, the Mössbauer parameter of the doublet pattern indicated the systematic change depending on the heat-treatment temperature. The isomer shift gradually decreased while the quadrupole splitting gradually increased with increasing the heat-treatment temperature. This result suggested the formation of strong Fe-O bonds and ligand fields due to the crystallization of LaFeO3 particles.

**Figure 8.** (a) TEM image and (b) its ED pattern of LaFeO3 nanoparticles obtained at 350°C. Diffraction rings are indexed as their corresponding LaFeO3 planes.


**Table 2.** Fitted Mössbauer parameters obtained from the spectra in Figure 9.

Magnetic measurements were performed on the heat-treated powders at various temperatures. The room-temperature magnetization curves of obtained samples are shown in Figure 10 as a function of the heat-treated temperature. LaFeO3 is known to be antiferromagnetic with weak ferromagnetism [8]. The net magnetization of LaFeO3 should be very small because of the antiferromagnetic order of the Fe3+ spins. Only a slight canting of the adjacent Fe3+ spins produced weak ferromagnetism. The spontaneous magnetization of LaFeO3 bulk crystals was only ~0.1 emu/g at room temperature [27]. However all samples seemed to have large magnetization, especially for the sample heat-treated at 350°C. The shape of hysteresis loops showing the small spontaneous magnetization were characteristics of weak ferromagnetism. The maximum field applied of 60 kOe did not saturate the magnetization. This was mainly caused by antiferromagnetic ordering of the spins in the nanoparticles [27]. By the way, the sample prepared at 500°C showed the remarkable hysteresis gap than the other samples. Mössbauer spectra indicated that only the sample prepared at 500°C possessed predominant antiferromagnetic ordering at room temperature while the others were paramagnetic. The small hysteresis gaps of the samples obtained at lower temperatures (325~450°C) supported their superparamagnetic nature.

382 Advanced Aspects of Spectroscopy

increasing the heat-treatment temperature. This result suggested the formation of strong Fe-

**Figure 8.** (a) TEM image and (b) its ED pattern of LaFeO3 nanoparticles obtained at 350°C. Diffraction

Quadupole splitting (mm/s)

325 0.329 0.891 - 100 300 0.327 0.824 - 100

Magnetic measurements were performed on the heat-treated powders at various temperatures. The room-temperature magnetization curves of obtained samples are shown in Figure 10 as a function of the heat-treated temperature. LaFeO3 is known to be antiferromagnetic with weak ferromagnetism [8]. The net magnetization of LaFeO3 should be very small because of the antiferromagnetic order of the Fe3+ spins. Only a slight canting of the adjacent Fe3+ spins produced weak ferromagnetism. The spontaneous magnetization of LaFeO3 bulk crystals was only ~0.1 emu/g at room temperature [27]. However all samples seemed to have large magnetization, especially for the sample heat-treated at 350°C. The shape of hysteresis loops

0.369 - 517 65 0.285 1.051 - 35

0.364 - 508 23 0.292 1.008 - 77

0.355 - 512 21 0.313 0.924 - 79

Hyperfine filed (kOe)

Intensity (%)

rings are indexed as their corresponding LaFeO3 planes.

Isomer shift (mm/s)

**Table 2.** Fitted Mössbauer parameters obtained from the spectra in Figure 9.

Heat-treatment temperature (°C)

500

450

350

O bonds and ligand fields due to the crystallization of LaFeO3 particles.

**Figure 9.** Room temperature Mössbauer spectra of the obtained products heat-treated at various temperatures.

The temperature dependence of magnetization behaviors under zero-field-cooling (ZFC) and field-cooling (FC) conditions measured in an external magnetic field of 200 Oe are shown in Figure 11. Magnetization of LaFeO3 particles obtained at 500°C was gradually decreased with decreasing the temperature. This behavior was characteristic of the antiferromagnetic ordered states below the TN. The higher TN above the room temperature was confirmed by the Mössbauer spectroscopy. The difference of magnetization values between ZFC and FC curves was attributed to the residual paramagnetic components at room temperature. On the other hand, magnetization of other samples obtained at 300~450°C were smoothly increased

**Figure 10.** Room temperature magnetization curves of the obtained products heat-treated at various temperatures.

with the decreasing temperature. These behaviors were very consistent with the paramagnetic nature of the obtained samples at room temperature. Moreover, the sharp cusps in the ZFC curves were observed for the samples obtained at 325~450°C. These were considered to be the superparamagnetic blocking temperature (TB), where the magnetization of LaFeO3 nanoparticles begun to freeze [28]. The TB detected by the ZFC curves was summarized in Table 3. It was decreased steeply with decreasing the heat-treatment temperature coincident with the decreasing particle sizes. Besides, the observed TB values were very small, which indicated that the magnetic interactions between the obtained LaFeO3 nanoparticles were very weak. The surface of LaFeO3 nanoparticles was probably coated with the residual organic molecules to form the non-magnetic layers [29]. This assumption was fully supported by the IR spectra indicating the presence of carbonized components and the TEM micrograph showing the loosely aggregating LaFeO3 nanoparticles. It should be mentioned here that the sample heat-treated at 325°C indicated the superparamagnetism, showing the small cusp in the ZFC curve at 7.7 K. The sample seemed to contain the LaFeO3 nanoclusters, though it showed the non-crystalline XRD pattern. But the IR spectrum seemed to have good sensitivity to detect their formation as well as the magnetization measurement. By the way, in the case of conventional superparamagnetic behavior, the FC magnetization curves should increase continuously with decreasing the temperature below the TB. But the FC curve of the heat-treated sample at 450°C showed a small cusp on cooling as well as the ZFC curve. This behavior suggested that the antiferromagnetic interactions between nanoparticles were present [28]. Long-range antiferromagnetic order was developed in associate with the grain growth of the LaFeO3 nanoparticles.


**Table 3.** Blocking temperature (TB) obtained from the ZFC curves shown in Figure 11.

384 Advanced Aspects of Spectroscopy

temperatures.

**Figure 10.** Room temperature magnetization curves of the obtained products heat-treated at various

with the decreasing temperature. These behaviors were very consistent with the paramagnetic nature of the obtained samples at room temperature. Moreover, the sharp cusps in the ZFC curves were observed for the samples obtained at 325~450°C. These were considered to be the superparamagnetic blocking temperature (TB), where the magnetization of LaFeO3 nanoparticles begun to freeze [28]. The TB detected by the ZFC curves was summarized in Table 3. It was decreased steeply with decreasing the heat-treatment temperature coincident with the decreasing particle sizes. Besides, the observed TB values were very small, which indicated that the magnetic interactions between the obtained LaFeO3 nanoparticles were very weak. The surface of LaFeO3 nanoparticles was probably coated with the residual organic molecules to form the non-magnetic layers [29]. This assumption was fully supported by the IR spectra indicating the presence of carbonized components and the TEM micrograph showing the loosely aggregating LaFeO3 nanoparticles. It should be mentioned here that the sample heat-treated at 325°C indicated the superparamagnetism, showing the small cusp in the ZFC curve at 7.7 K. The sample seemed to contain the LaFeO3 nanoclusters, though it showed the non-crystalline XRD pattern. But the IR spectrum seemed to have good sensitivity to detect their formation as well as the magnetization measurement. By the way, in the case of conventional superparamagnetic behavior, the FC magnetization curves should increase continuously with decreasing the temperature below the TB. But the FC curve of the heat-treated sample at 450°C showed a small cusp on cooling as well as the ZFC curve. This

**Figure 11.** Temperature dependence of ZFC and FC magnetization curves at 200 Oe for the obtained products at various heat-treatment temperatures

In order to demonstrate the superparamagnetic behavior more directly, we measured the temperature dependence of their Mössbauer spectra down to 15 K. Figure 12(a) shows the typical law temperature Mössbauer spectra of the LaFeO3 nanoparticles obtained at 350°C. The spectrum measured at room temperature (see Figure 9) was well consistent with that of the LaFeO3 nanoparticles with average grain size of 16 nm reported in literature [26]. The spectrum was mainly composed of the super-paramagnetic doublet peak besides to the magnetically split sextet. The component showing the sharp sextet pattern could be attributed to the unexpected coarse LaFeO3 particles which had a good crystallinity, while the most of the particles exhibited the paramagnetic doublet pattern at room temperature. With decreasing the temperature, the paramagnetic spectra corresponded to the enlarged sextets due to the presence of magnetic order. Therefore the spectra were decomposed into three components. One was the sharp sextet for the coarse particles; second and third were the broad sextet and paramagnetic doublet for the nanoparticles, respectively. Relative intensity ratio of each component was plotted in Figure 12(b) as a function of the temperature. The relative area of the paramagnetic component varies almost linearly with decreasing the temperature below 100 K. According to the Mössbauer measurements, we defined the

**Figure 12.** (a) Low temperature Mössbauer spectra of LaFeO3 nanoparticles obtained at 350°C, and (b) relative area of each component as a function of the temperature. The details are described in the text.

median blocking temperature (TB*m*), as a temperature where the doublet collapsed to 50% of its initial value. This analysis yielded the TB*m* of ~50 K, which was much higher than the superparamagnetic TB obtained by the magnetization measurement. It was well-known that the time scale of the superparamagnetic fluctuations becomes comparable to the time scale of the measurement [30]. The time scale of Mössbauer measurements (~10-9 s) was much faster than that of magnetization measurements (~10-1 s) and gave the higher TB*m* well above the TB. This phenomenon evidenced the presence of superparamagnetic relaxation of the obtained samples.

386 Advanced Aspects of Spectroscopy

In order to demonstrate the superparamagnetic behavior more directly, we measured the temperature dependence of their Mössbauer spectra down to 15 K. Figure 12(a) shows the typical law temperature Mössbauer spectra of the LaFeO3 nanoparticles obtained at 350°C. The spectrum measured at room temperature (see Figure 9) was well consistent with that of the LaFeO3 nanoparticles with average grain size of 16 nm reported in literature [26]. The spectrum was mainly composed of the super-paramagnetic doublet peak besides to the magnetically split sextet. The component showing the sharp sextet pattern could be attributed to the unexpected coarse LaFeO3 particles which had a good crystallinity, while the most of the particles exhibited the paramagnetic doublet pattern at room temperature. With decreasing the temperature, the paramagnetic spectra corresponded to the enlarged sextets due to the presence of magnetic order. Therefore the spectra were decomposed into three components. One was the sharp sextet for the coarse particles; second and third were the broad sextet and paramagnetic doublet for the nanoparticles, respectively. Relative intensity ratio of each component was plotted in Figure 12(b) as a function of the temperature. The relative area of the paramagnetic component varies almost linearly with decreasing the temperature below 100 K. According to the Mössbauer measurements, we defined the

**Figure 12.** (a) Low temperature Mössbauer spectra of LaFeO3 nanoparticles obtained at 350°C, and (b) relative area of each component as a function of the temperature. The details are described in the text. Figure 13 shows the field dependent magnetization curves measured at lower temperature (5 K) for the LaFeO3 nanoparticles prepared at various heat-treatment temperatures. The samples showed considerable magnetization at low temperature, though the net magnetization of LaFeO3 bulk crystals should be very small because of the antiferromagnetic order of the Fe3+ spins. A spontaneous magnetization of the bulk crystals was evaluated to 0.15 emu/g at 5 K [16]. We have recently reported that the LaFeO3 nanoparticles prepared at 350°C revealed an anomalous large spontaneous magnetization of 7.8 emu/g [16]. This phenomenon was almost reproducible. The spontaneous magnetization of the obtained powders exhibited the maximum value for the samples prepared at 350°C. The LaFeO3 nanoparticles with the average diameter of ~15 nm seemed to have large ferromagnetism instead of antiferromagnetism. The induced ferromagnetism in LaFeO3 nanoparticles was possibly associated with the uncompensated surface spins as reported in other antiferromagnetic nanocrystalline systems [9, 10]. It should be worth to mention that the induce magnetic moment per Fe3+ ion was evaluated to 0.34B for the sample obtained at 350°C. Taking into account that the moment of Fe3+ is 5B, a large fraction (~7%) of Fe3+ ions contribute to the magnetization of LaFeO3 nanoparticles. Magnetic structure of LaFeO3 nanoparticles should be strongly modified from the bulk one.

By the way, all magnetization curves revealed clear hysteresis gaps with small loop shifts at 5 K. The coercivity and the exchange bias field of each sample are summarized in Table 4 as well as the spontaneous magnetization. The exchange field was linearly increased with increasing the heat-treatment temperature. The exchange bias was generally attributed to the exchange coupling between the ferromagnetic shell and the antiferromagnetic core of the particles [31]. In the case of LaFeO3 particles, the uncompensated surface spins and/or the enhanced spin cantings near the surface region should cause the considerable magnetization. With the increasing particle size, the reliable antiferromagnetic core was formed to produce the large exchange coupling.


**Table 4.** Magnetic parameters at 5 K of the obtained products at various heat-treatment temperatures.

**Figure 13.** Low temperature (5 K) magnetization curves of the obtained products heat- treated at various temperatures. The insets are the enlarged view of the central region.
