International Journal of Engineering Materials and Manufacture (2019) 4(3) 96-106 

https://doi.org/10.26776/ijemm.04.03.2019.02 

 

E. Sukirman
1
 , Y. Sarwanto

1
, W. Ari Adi

1
, A. Insani

1
 and Y. F. Buys

2
 

1
Centre for Science and Technology of Advance Materials-BATAN 

Puspiptek, Serpong 15314, Indonesia. 

E-mail: skm2792@batan.go.id 

 

2
University of Malaya, Jalan Universiti, 50603 Kuala Lumpur 

Wilayah Persekutuan Kuala Lumpur, Malaysia. 

E-mail: yose@um.edu.my 

 

Reference: Sukirman, E., Sarwanto, Y., Ari Adi, W., Insani, A., and Buys, F. Y. (2019). Weak Ferromagnetic Property and 

Electromagnetic Waves Absorption Characteristic of La(1-x)BaxMnO3. International Journal of Engineering Materials and 

Manufacture, 4(3), 96-106 

 

 

Weak Ferromagnetic Property and Electromagnetic Waves Absorption 

Characteristic of La(1-x)BaxMnO3 

 

 

E. Sukirman, Y. Sarwanto, W. Ari Adi, A. Insani, and Y. Fachmi Buys 

 

 

Received: 23 May 2019 

Accepted: 30 August 2019 

Published: 27 September 2019 

Publisher: Deer Hill Publications 

© 2019 The Author(s) 

Creative Commons: CC BY 4.0 

 

 

ABSTRACT 

The weak ferromagnetic property and the electromagnetic waves absorption characteristic of La(1-x)BaxMnO3 (LBMO) 

compounds have been investigated. The samples of LBMO that are LaMnO3 (S0), La0.9Ba0.1MnO3 (S1); La0.8Ba0.2MnO3 

(S2); and La0.7Ba0.3MnO3 (S3) were synthesized using high energy milling (HEM) method. Samples were characterized 

by means of XRD (X-ray diffractometer), HRPD (high-resolution powder neutron diffractometer), EDS (energy 

dispersive X-ray spectroscopy, VSM (vibrating sample magnetometer), and VNA (vector network analyzer). There 

is no magnetic ordering of ferromagnetic in S1 and S2 samples due to the Ba occupation factors of both less than 

0.2. The Ba content in the S3 sample is greater than 0.2, hence the ferromagnetic property of the compound is not 

so visible with the VSM as well as the VNA. The absorption characteristics of electromagnetic waves using VNA 

indicated that there is an absorption of EM waves in the frequency range between 8-12 GHz with almost the same 

peak frequency for all four samples at 10.8 GHz with the absorption of around 5 dB. The existence of a weak 

ferromagnetic property can be detected clearly using HRPD. Neutron diffraction as a probe can observe the magnetic 

structure accurately even in a material having a weak ferromagnetic property. 

 

Keywords: La-manganite, Ba-substitution, cystal structure, electromagnetic wave absorber, weak ferromagnetic. 

 

1 INTRODUCTION 

Generally, the parent compound, LaMnO3 with perovskite ABO3 structure has antiferromagnetic insulator properties 

in which Mn is present in a single oxidation state (Mn
+3

). It is found that the stable phase is the antiferromagnetic A-

type, which corresponds to the ferromagnetic order of the manganese ions in the basal planes (a, b) and 

antiferromagnetic order of these ions between these planes along the c axis [1]. The conductivity of rare-earth 

manganese oxides is enhanced to approach that of metal or semiconductor from the insulating state when doped 

and their colossal magnetoresistance effect (CMR) is remarkable [2]. Therefore, they are fascinating to be studied and 

applied on a large scale due to their unusual electromagnetic properties [3−5]. Besides that due to the unusual 

magnetic and electronic properties of the LaMnO3 compound, one can develop a very good electromagnetic wave 

absorbing device [6-8]. 

Luckily, the desired properties of LaMnO3 can be tuned easily by partial substitution of the trivalent rare-earth 

element (La
3+

) with divalent alkaline earth elements, such as Ba
2+

 forming a new compound of La(1-x)BaxMnO3 

(LBMO). The property as a microwave absorber of this manganite is usually obtained by varying the concentration 

of Ba
2+

 element [3]. Substitutions at the trivalent rare  earth  site (A-site) by a divalent alkaline earth metal ion like 

Ca, Sr, Ba or Pb causes part of the Mn
+3

 are oxidized to Mn
+4

 ions and  transforms this compound to a ferromagnetic 

metal [9]. In order, the electric charge of the compound to remain neutral, a number of Mn
3+

 ions donate some of 

its electrons to Mn
4+

 and therefore formed a mixed valence system of [𝑳𝒂(𝟏−𝒙)
𝟑+ 𝑩𝒂𝒙

𝟐+][𝑴𝒏(𝟏−𝒚)
𝟑+ 𝑴𝒏𝒚

𝟒+]𝑶𝟑
𝟐−. The 

ferromagnetic behaviour occurred due to magnetic interactions between Mn
3+

 and Mn
4+

 ions through the double-

exchange mechanism [10]. 



Sukirman et al., (2019): International Journal of Engineering Materials and Manufacture, 4(3), 96-106 

97 

The previous studies [11] showed that a strong ferromagnetism of LBMO compound occurred at x ≈ 0.2, and at x > 

0.2 the properties of ferromagnetic materials become weak, while at x < 0.2 the material becomes antiferromagnetic 

at room temperature. The purpose of this research is to determine the crystal structure, and to observe a weak 

ferromagnetic property of magnetic material in relation with the electromagnetic waves absorption characteristic of 

La(1-x) BaxMnO3 (LBMO) compounds. It will be carried out using the neutron diffraction method, under the assumption 

that it could not be done by any other method. No studies have ever been done so far to prove the problem. In this 

study, the LBMO samples were synthesized by solid-state reaction method using High Energy Milling (HEM) process. 

 

2 METHODOLOGY 

The samples were prepared by using solid- state reaction method to the raw materials of La2O3, BaCO3, and MnO2, 

where the purity of La2O3 raw material is 99.5 % from local products and the remaining two raw materials have 

more than 99.9 % purity from Merck products. The solid reaction in this research was conducted through high energy 

milling (HEM) process with the same procedure as before [12].  Subsequently, the precursors were sintered at 1200C 

for 5 hours at a heating rate of around 49C/min and the cooling was carried out naturally to room temperature in 

the furnace. 

It was synthesized four kinds of samples of La1-xBaxMnO3 that are LaMnO3 (S0), La0.9Ba0.1MnO3 (S1), 

La0.8Ba0.2MnO3 (S2), and La0.7Ba0.3MnO3 (S3). Phase characterization was then performed with X-ray diffractometer 

(XRD), type of PW1710 Philips with cooper anode tube, = 1.5406 Å, the data were collected in the scattering 

angular range of 10
o
 up to 100

o
 in the interval of 0.02

o
 at room temperature. The phase was also characterized using 

high-resolution powder neutron diffractometer (HRPD) with =1.8216 Å. The sample was loaded into a cylindrical 

vanadium holder. The data was collected in the scattering angular range of 2.5
o
 up to 157

o
 in the interval of 0.05

o
 

at room temperature. The XRD data were analysed with the help of general structure analysis system (GSAS) and the 

neutron diffraction data was refined using the FullProof software. The elementary analysis was performed using 

scanning electron microscope (SEM) and energy dispersive X-ray spectroscopy (EDS) of JEOL instrument. 

The electromagnetic waves absorption characteristics of the samples were analysed by using vector network 

analyser (VNA) of ADVANTEST R3770 types with the frequency range of 300 kHz - 20 GHz.  The magnetic 

properties of materials were characterized using vibrating sample magnetometer (VSM), Oxford Type 1.2 Hin 

method. Measurement of magnetic properties of materials was made in an applied magnetic field to a maximum 

value of 1 Tesla. VSM measurements were carried out at room temperature. Measurements, XRD, HRPD, VSM and 

SEM / EDS were performed at the Centre for Advanced Materials Science and Technology (PSTBM), BATAN, 

Puspiptek, Setu, Tangerang Selatan. While the measurements of VNA were done at the Centre for Electronic Research 

and Telecommunications (PPET), LIPI, Bandung. 

 

3 RESULTS AND DISCUSSIONS 

The Rietveld analysis based on the X-ray diffraction data using GSAS software from the LaMnO3, La0.9Ba0.1MnO3, 

La0.8Ba0.2MnO3, and La0.7Ba0.3MnO3. Samples were showed in Figure 1(S0), 1(S1), 1(S2) and 1(S3), respectively. The 

diffraction pattern of S0 exhibited a single phase diffraction profile within the limits of accuracy of the tool.  The dots 

are the observed intensity, the solid line was the calculated intensity, and the difference pattern was shown at the 

bottom of the chart. The S0 sample crystallizes into the space group: I12/a1, with 2 = 1.3 and the lattice parameters: 

a = 7.7839(5) Å, b = 5.5288(4) Å, c = 5.4781(3) Å,  = 90˚,  = 90.746(2)˚,  = 90.0˚ and volume, V = 235.73(4) 

Å
3
.  The coordinates of the atomic fractions were shown in Table 1. The smoothing on the occupancy factor of 

oxygen atoms caused their value to be greater than 1.0. According to previous research [11], the S0 sample should 

display the properties as a paramagnetic material. This will be proved by measurement using VSM. 

The diffraction pattern of S1 sample which was the result of analysis by Rietveld method was shown in Figure 

1(S1). The S1 samples also showed a single phase diffraction pattern within the limits of accuracy of the tool. It was 

obtained a better fitting result with 2 = 1.3. The S1 sample crystallized also into the space group: I12/a1 in accordance 

with the results of previous research [11], the lattice parameters: a = 7.8142(9) Å, b = 5.5462(6) Å, c = 5.4993(6) 

Å,  = 90˚,    = 90.593(5)◦,   = 90◦  and  volume, V = 238.33(7) Å3. The atomic fraction coordinates (xj, yj, zj), 

and the atomic occupancy factor (gj) of S1 sample was indicated in Table 2. The mole fraction of La and Ba that were 

0.86, and 0.105, respectively, correspond to the weighed mole fraction on the synthesis that was 0.9 and 0.1, 

respectively. The occupation factors of Mn, O(1) and O(2) were not refined, because the smoothing caused their 

value to be greater than 1.0. 

 

 

Table 1. The coordinates of atomic fractions (xj, yj, zj), and atomic occupancy factor (gj) of S0 sample. 

 

Atom gj xj yj zj 

La 0.810(1) 0.25 0.5066(6) 0.0 

Mn 0.85(2) 0.0 0.0 0.0 

O(1) 1.0 0.25 0.0 0.0 

O(2) 1.0 -0.013(2) 0.198(3) 0.292(4) 



Weak Ferromagnetic Property and Electromagnetic Waves Absorption Characteristic of La(1-x)BaxMnO3 

98 

 

 

 

Figure 1. The X-ray diffraction pattern of LaMnO3 (S0), La0.9Ba0.1MnO3 (S1), La0.8Ba0.2MnO3 (S2), and La0.7Ba0.3MnO3 

(S3). 

 

Based on the results of previous research [11], the S1 sample should display the properties as an antiferromagnetic or 

a paramagnetic instead of ferromagnetic material due to the occupation factor of Ba was smaller than 0.2. This will 

be proved by measurement using VSM. The pattern of diffraction after analysis by Rietveld method of S2 sample was 

showed in Figure 1(S2). It appeared on the figure that the sample displayed a single phase diffraction pattern to the 



Sukirman et al., (2019): International Journal of Engineering Materials and Manufacture, 4(3), 96-106 

99 

extent of the accuracy of the tool. The S2 sample crystallized into the space group: I12/c1 in accordance with the 

results of previous research [11], with the goodness of fitting, 2 = 1.2, the lattice parameters: a = 5.5118(3) Å, b = 

5.5401(4) Å, c = 7.8244(4) Å,  = 90◦,  = 90.447(6)◦,  = 90◦ and volume, V = 238.92(1)Å3. The atomic fraction 

coordinates (xj, yj, zj), and the atomic occupancy factor (gj) of S2 sample were indicated in Table 3. The occupation 

factor of oxygens was not refined, because the smoothing caused their value to be greater than 1.0. 

The atomic fraction coordinates of O(2) were not refined, because when those parameters were smoothed caused 

the chi- square enlarged. It appeared in Table 3 that the S2 lacked La and Ba atoms in its unit cell that were 0.65 and 

0.17, respectively. The mole fraction of La and Ba atoms did not correspond to the weighed mole fraction on the 

synthesis that was 0.8 and 0.2, respectively. The previous studies [11] showed that a strong ferromagnetism of LBMO 

compound occurred when the Ba occupation factor of x ≈ 0.2, and at x < 0.2 the material becomes 

antiferromagnetic. Thus, S2 sample should also display the properties as an antiferromagnetic or a paramagnetic 

material instead of ferromagnetic one due to the occupation factor of Ba
2+

 ion was smaller than 0.2. This will be 

proved by measurement using VSM. 

The diffraction pattern after being analysis by the Rietveld method of S3 sample was shown in Figure 1(S3). It 

appeared on the figure that there was a peak of foreign phase at 2 ≈ 36˚, where this peak was marked with symbol 

. Based on XRD data, the presence of this foreign phase cannot be analysed, possibly because the amount is smaller 

than the XRD detection limit. Table 4 was the coordinates of atomic fractions (xj, yj, zj), and atomic occupantion 

factor (gj) of S3 sample. It appeared in this table that the occupation factor (gj) of La and Ba atoms in its unit cell 

ware 0.61 and 0.22, respectively. Thus, the S3 sample should displays a weak ferromagnetic property due to gj of 

Ba
2+

 ion was greater than 0.2, this will be proved later. 

The S3 sample crystallized into the space group: R-3c in accordance with the results of previous research [13], 

with the goodness of fitting, 2 = 1.6  and  the  lattice parameters: a = b = 5.5301(7) Å, c = 13.532(3) Å,  =  = 

90
˚
,  = 120˚, volume, V = 358.41(9) Å3. The occupation factor of oxygen was not refined, because the smoothing 

caused its value to be greater than 1.0. 

 

 

Table 2. The coordinates of atomic fractions (xj, yj, zj), and atomic occupancy factor (gj) of S1 sample. 

 

Atom gj xj yj zj 

La 0.86(1) 0.25 0.502(1) 0.0 

Ba 0.105(4) 0.25 0.502(1) 0.0 

Mn 1.0 0.0 0.0 0.0 

O(1) 1.0 0.25 0.0 0.0 

O(2) 1.0 -0.017(4) 0.204(4) 0.281(5) 

 

 

Table 3. The coordinates of atomic fractions (xj, yj, zj), and atomic occupancy factor (gj) of S2 sample. 

 

Atom gj xj yj zj 

La 0.65(1) 0.0 0.499(2) 0.75 

Ba 0.17(3) 0.0 0.499(2) 0.75 

Mn 0.853(9) 0.0 0.0 0.0 

O(1) 1.0 0.0 0.056(3) 0.25 

O(2) 1.0 0.251 0.249 -0.03 

 

 

Table 4. The coordinates of atomic fractions (xj, yj, zj), and atomic occupancy factor (gj) of S3 sample. 

 

Atom gj xj yj zj 

La 0.61(1) 0.0 0.0 0.25 

Ba 0.22(1) 0.0 0.0 0.25 

Mn 0.92(2) 0.0 0.0 0.0 

O 1.0 0.480(6) 0.0 0.25 

 

 

Figure 2 showed the EDS spectrum of S0, S1, S2, and S3. The four samples showed an identical EDS spectrum. Table 

5 was the mass fraction of the elements in S0, S1, S2, and S3 samples which were based on the number of counts 

each peak of the EDS spectrum. Then the mass fraction of Ba elements in S1, S2 and S3 were then converted into the 

mole fraction of Ba elements, the result was showed in Table 6. 

It appeared in Table 6 that the mole fraction of Ba elements in S1 and S2 showed by EDS data in accordance to 

data of XRD and also in accordance to the one on weighing, that was 0.1 and 0.2, respectively. This means that on 



Weak Ferromagnetic Property and Electromagnetic Waves Absorption Characteristic of La(1-x)BaxMnO3 

100 

both samples, the Ba atoms have entered into the unit cell of LaMnO3.The mole fraction of the XRD data is the mole 

fraction per unit cell, whereas the mole fraction of the EDS data is the one of the element present in the sample. The 

mole fraction of the Ba element in S3 showed by EDS data was in accordance with the one on weighing, i.e., 0.3, 

but was incompatible with XRD data, i.e., 0.2.  It was concluded that there was about 0.1 mole of Ba elements not 

entering into the unit cell of LaMnO3, but forming a new phase. A foreign peak on Figure 1 (S3) appearing at 2 ≈ 

36˚ was assumed to belong to the new phase formed by Ba elements. 

 

 

Table 5. The mass fraction of O, Mn, Ba and La elements in S0, S1, S2, and S3 samples. 

 

 Energy Mass fraction (%) 

Element (keV) S0 S1 S2 S3 

O 0.525 18.68 

0.09 

17.88 

0.07 

22.23 

0.06 

18.94 

0.07 

Mn 5.894 21.72 

0.25 

23.65 

0.19 

19.76 

0.18 

20.94 

0.21 

Ba 4.464 - 5.67 

0.25 

10.06 

0.23 

17.16 

0.27 

La 4.648 59.60 

0.35 

52.80 

0.29 

47.95 

0.27 

42.96 

0.31 

 

 

 

 

Figure 2. The EDS spectrum of LaMnO3 (S0), La0.9Ba0.1MnO3 (S1), La0.8Ba0.2MnO3 (S2), and La0.7Ba0.3MnO3 (S3). 

 



Sukirman et al., (2019): International Journal of Engineering Materials and Manufacture, 4(3), 96-106 

101 

Table 6. The mole fraction of Ba element in S1, S2, and S3 samples result from the conversion of its mass fraction. 

 

 Mole fraction of Ba element. 

Sample weighing XRD EDS 

S1 0.1 0.105(4) 0.098(2) 

S2 0.2 0.17(3) 0.170(2) 

S3 0.3 0.22(1) 0.283(2) 

 

 

 

 

 

Figure 3. The microwave absorbing characteristics of the S0, S1, S2 and S3 samples in the range of 2-12 GHz. 

 

 

The interaction of the ceramics with electromagnetic waves characterized by using an HP8720B vector network 

analyser in the frequency range of 2-12 GHz was shown in Figure 3. The results revealed that the electromagnetic 

wave absorption characteristics of S0, S1, S2, and S3 were almost the same, i.e., showing the same reflection loss 

peaks of around -5 dB at a frequency of 10.8 GHz. The microwave absorption primarily resulted from magnetic 

losses caused by magnetization relaxation, domain wall resonance, and natural resonance [14]. This means that all 

four samples have the same magnetic properties, i.e., as an antiferromagnetic or a paramagnetic materials, because 

they do not display significant reflection loss, where the previous research [11] showed only manganite with the 

magnetic ordering of ferromagnetic has the best ferromagnetic properties and therefore display the best characteristic 

in absorbing an electromagnetic wave. 

The curves showing the relation between magnetization, M to magnetic field, H, commonly called magnetization 

curves, for the four samples were shown in Figure 4. It was exhibited that S0, S1, and S2 samples displayed a typical 

pattern for the antiferromagnetic materials, i.e., displaying the linear curve of M vs H.  While the M vs. H curve of 

S3 does not perfectly display a straight line, but slightly curved to form an incomplete S letter.  This is in accordance 

with the results of previous studies [11] which showed that the LBMO compounds, whose the Ba occupation factors 

of gj less than, or greater than 0.2 were antiferromagnetic, or weak ferromagnetic materials, respectively. 

The presence of a paramagnetic, antiferromagnetic or ferromagnetic phase in LBMO samples was then 

investigated by neutron diffraction technique using the Rietveld analytical methods with the help of FullFrof software. 

Based on the XRD data, the three samples of S0, S1, and S2 have the monoclinic crystal structure, while S3 sample 

crystallized with hexagonal structure. The analysis of neutron diffraction data, therefore, was performed on S0 only 

because the three samples are identical. Analysis of neutron diffraction data was also carried out on S3 with a purpose 

besides to confirm the presence of antiferromagnetic or weak ferromagnetic phases also to confirm the presence of 

foreign phase. 

First, it was carried out the analysis of nuclear structure with input parameters equal to the input parameters in 

XRD data analysis using GSAS software. The results show that all of the diffraction peaks coincide with the calculation 

results based on the nuclear peaks (Figure 5). This means there are no additional peaks due to scattering from the 

magnetic phase. So the magnetic structure would have a propagation vector k = (0,0,0). As the propagation vector 

is k = (0,0,0), the magnetic unit cell is identical to the nuclear cell. 



Weak Ferromagnetic Property and Electromagnetic Waves Absorption Characteristic of La(1-x)BaxMnO3 

102 

Next, the BasIRreps program was employed to determine the basis vectors of the irreducible representations (IRreps) 

of the propagation vector group (Gk). With the help of this program one can determine the appropriate magnetic 

symmetry and the magnetic rotation vectors. The output of the calculation for the basic functions of IRreps 

corresponding to the experimental magnetic structure of LaMnO3 with space group: I12/a1 are a basic function of 

IRreps (1) for antiferromagnetic structures (Table 7) and IRreps (3) for ferromagnetic structures (Table 8). 

 

 

 

 

Figure 4. The curve for magnetization, M to magnetic field, H from sample LaMnO3 (S0), La0.9Ba0.1MnO3 (S1), 

La0.8Ba0.2MnO3 (S2), and La0.7Ba0.3MnO3 (S3). 

 

 

 

 

Figure 5. Neutron diffraction patterns of LaMnO3 (S0), the Rietveld analysis results based on the nuclear phase only 

without involving magnetic phase, with 2 = 1.9 
 

 

Table 7. Basis functions of Representation IRrep (1) of LaMnO3, space group: I12/a1, magnetic symmetry (SYMM), 

magnetic rotation vector (Sk), fractional coordinates (xj, yj, zj) of Mn(1), and Mn(2) atoms. 

 

Atoms Mn(1) Mn(2) 

(xj, yj, zj) (0.0, 0.0, 0.0) (0.5, 0.0, 0.0) 

SYMM (x, y, z) (-x+1/2, y, -z) 

Sk (u, v, w) (-u, v, -w) 

 



Sukirman et al., (2019): International Journal of Engineering Materials and Manufacture, 4(3), 96-106 

103 

Thus, analysis of the magnetic structure on LaMnO3 was carried out by trial and error, first input the data in Table 7 

followed by the data in Table 8 to determine which data will give the smallest 2. The chi-square of the neutron 

diffraction patterns of S0 using the IRreps(1) and IRreps(3) are 1.8 and 2.6, respectively. Thus, S0 has a magnetic 

ordering of antiferromagnetic, where the lattice of magnetic ions in the crystal breaks up into two sublattices along 

the a-axis having magnetic moments,  = 1.7(5) B in opposite directions (Figure 6). This result is in agreement with 

VSM data and  in accord with the previous research indicated by Priyo Sardjono et. al. [11]. 

Figure 7 is the neutron diffraction patterns of S0 based on two phases, namely the nuclear-, and magnetic phase using 

basis functions of IRreps(1). The S0 sample crystallizes into single phase of LaMnO3, space group: I12/a1, and the 

lattice parameters: a = 7.8217(7) Å, b = 5.5458(5) Å, c = 5.5230(6) Å,  =  = 90°, and  = 90.217(7)°. The vertical 

short lines closest to the horizontal axis indicate the position of the peaks of nuclear scattering, while the vertical 

short lines below them are the position of the peaks of the magnetic scattering. Table 9 was the coordinate of atomic 

fractions (xj, yj, zj), and atomic occupancy factors (gj) of LaMnO3 based on the neutron diffraction experiment. 

 

Table 8. Basis functions of Representation IRrep (3) of LaMnO3, space group: I12/a1, magnetic symmetry (SYMM), 

magnetic rotation vector (Sk), fractional coordinates (xj, yj, zj) of Mn(1), and Mn(2) atoms. 

 

Atoms Mn(1) Mn(2) 

(xj, yj, zj) (0.0, 0.0, 0.0) (0.5, 0.0, 0.0) 

SYMM (x, y, z) (-x+1/2, y, -z) 

Sk (u, v, w) (u, -v, w) 

 

 

 

Figure 6. The antiferromagnetic structure of LaMnO3. 

 

 

 

 

 

Figure 7. Neutron diffraction patterns of LaMnO3 (S0), the Rietveld analysis results based on the nuclear- and 

magnetic phase using basis functions of IRreps (1), with 2 = 1.8. 



Weak Ferromagnetic Property and Electromagnetic Waves Absorption Characteristic of La(1-x)BaxMnO3 

104 

Table 9. The coordinates of atomic fractions (xj, yj, zj), and atomic occupancy factor (gj) of S0 sample based on 

neutron diffraction data. 

 

Atom gj xj yj zj 

La 0.4(7) 0.25 0.509(2) 0.0 

Mn 0.6(7) 0.0 0.0 0.0 

O(1) 0.2(4) 0.25 0.0 0.0 

O(2) 1.0 0.0 0.220(1) 0.267(2) 

 

 

Table 10. Basis functions of Representation IRrep (1) of LaMnO3, space group: R-3c, magnetic symmetry (SYMM), 

magnetic rotation vector (Sk), fractional coordinates (xj, yj, zj) of Mn(1), and Mn(2) atoms. 

 

Atoms Mn(1) Mn(2) 

(xj, yj, zj) (0.0, 0.0, 0.0) (0.0, 0.0, 0.5) 

SYMM (x, y, z) (y, x, -z+1/2) 

Sk (0, 0, u) (0, 0, -u) 

 

 

Table 11. Basis functions of Representation IRrep (3) of LaMnO3, space group: R-3c, magnetic symmetry (SYMM), 

magnetic rotation vector (Sk), fractional coordinates (xj, yj, zj) of Mn(1), and Mn(2) atoms. 

 

Atoms Mn(1) Mn(2) 

(xj, yj, zj) (0.0, 0.0, 0.0) (0.0, 0.0, 0.5) 

SYMM (x, y, z) (y, x, -z+1/2) 

Sk (0, 0, u) (0, 0, u) 

 

 

 

(a) 

 

(b) 

Figure 10. The antiferromagnetic structure (a), and ferromagnetic structure (b) of Ba-doped LaMnO3 (S3). 

 

Furthermore, magnetic structural analysis of S3 was done as for S0 above. The output of the calculation for the 

basis functions of IRreps corresponding to the experimental magnetic structure of LaMnO3 with space group: R-3c 

are basis functions of IRreps(1) for antiferromagnetic structures (Table 10) and IRreps(3) for ferromagnetic structures 

(Table 11). The result of observation by means of Match software of S3 shows the existence of a new phase of 

BaLa2O4. This X-ray diffraction data of the BaLa2O4 phase could not be analyzed by GSAS software, presumably due 

to its small content. The presence of BaLa2O4 phase was then observed by HRPD together with the nuclear and 

magnetic phases.  

Analysis of the magnetic structure on S3 was carried out with the input parameters of Table 10 and Table 11 

simultaneously. This step was carried out because in S3 other than the nuclear phase of LBMO and BaLa2O4 phase, it 

is also assumed that there are two magnetic phases, namely antiferromagnetic- and ferromagnetic phase. The analysis 

of neutron diffraction data using the Rieveld method utilizing FullProf software shows that S3 has two magnetic 

phases, namely the ferromagnetic and antiferromagnetic phases with the chi-square of the neutron diffraction pattern 

of S3 is 1.7. The sample of S3 has magnetic ordering of antiferromagnetic and ferromagnetic with the magnetic 

moment,  = 1.9(2) B (Figure 10).  

The VSM data reveals that the M vs. H curve of S3 does not perfectly display a straight line, but slightly curved 

to form an incomplete S letter. This means that S3 is not a pure antiferromagnetic material. This material imperfection 

is apparently still detected by neutron diffraction methode as a material that has a composition of atoms such as 



Sukirman et al., (2019): International Journal of Engineering Materials and Manufacture, 4(3), 96-106 

105 

ferromagnetic order, although weak. This result is in agreement with the results of previous research indicated by 

Priyo Sardjono et. al [11] and Sukirman et al [15]. 

Figure 11 is the neutron diffraction patterns of S3 based on four phases, namely the nuclear-, antiferromagnetic-, 

ferromagnetic-, and BaLa2O4 phase after being analyzed with FullProf software with the goodness of fitting,  2 = 

1.7 and the coordinates of the atomic fractions was showed on Table 12. Rows of the vertical short lines closest to 

the horizontal axis indicate the position of the peaks of nuclear scattering, while the vertical short lines below them 

are the position of the peaks of the magnetic scattering, and the third row below is the peak positions of BaLa2O4 

phase.  

The atomic occupancy factors (gj) on Table 12 corresponded to the one on Table 4 which showed that the mole 

fraction of La and Ba atoms in the unit cell of the LBMO compound were each smaller than their value when weighed 

at the time of the synthesis. This was an evidence that some of the atoms of Ba and La did not enter into the unit cell 

of the compound, but form a new compound, i.e., BaLa2O4, Space Group: Pnam (No. 62), lattice parameters: a = 

10.621(2) Å, b = 12.466(3) Å, c = 3.7191(6) Å,  =  =  = 90˚. Table 13 were the coordinates of atomic fraction 
(xj, yj, zj), and atomic occupancy factors (gj) of BaLa2O4 phase based on neutron diffraction data. It can be concluded 

that with the support of neutron diffraction data, the reflection loss versus frequency curve (Figure 3) and 

magnetization versus magnetic field curves (Figure 4) are both corresponding. 

 

 

Figure 11. Neutron diffraction patterns  of  S3, Rietveld analysis results based on the nuclear- and magnetic phase 

using basis functions of IRreps(3), with 2 = 1.7. 

 

 

Table 12. The coordinates of atomic fractions (xj, yj, zj), and atomic occupancy factor (gj) of S3 sample based on 

neutron diffraction data. 

 

Atom gj xj yj zj 

La 0.6(1) 0.0 0.0 0.25 

Ba 0.23(1) 0.0 0.0 0.25 

Mn 0.6(2) 0.0 0.0 0.0 

O 1.0 0.4731(6) 0.0 0.25 

 

Table 13. The coordinates of atomic fractions (xj, yj, zj), and atomic occupancy factor (gj) of  BaLa2O4 phase based 

on neutron diffraction data. 

 

Atom gj xj yj zj 

Ba 0.164 0.220(3) 0.660(2) 0.25 

La(1) 0.147 0.04(1) 0.44(1) 0.25 

La(2) 0.367 0.651(7) 0.584(6) 0.25 

O(1) 0.828 0.243(4) 0.253(5) 0.25 

O(2) 0.636 0.414(7) 0.032(5) 0.25 

O(3) 0.597 0.547(6) 0.764(5) 0.25 

O(4) 0.593 0.022(6) 0.123(4) 0.25 



Weak Ferromagnetic Property and Electromagnetic Waves Absorption Characteristic of La(1-x)BaxMnO3 

106 

4 CONCLUSIONS 

In this study, the La(1-x)BaxMnO3 (LBMO) sample’s magnetic ordering dependence on the Barium mole fraction has 

been verified by way of experimental investigation and analysis  on its weak ferromagnetic property and its 

electromagnetic wave absorption characteristic. If the mole fraction of Ba in LBMO is smaller than 0.2, the sample is 

classified as an antiferromagnetics, on the other hand  if the mole fraction of Ba is greater than 0.2 the material is then 

classified as having  a weak ferromagnetic property. Experimental evidence of the formation of weak ferromagnetic 

property of the LBMO in its unit cell could readily be obtained by using the neutron diffraction technique. However, 

in the frequency range between 8-12 GHz, the electromagnetic waves absorption of both antiferromagnetic and weak 

ferromagnetic compounds occurs at around 10.8 GHz with the absorption of around 5 dB. The mole fraction of 

Barium has also been found to affect the LBMO phase formation, the magnetic properties, and the electromagnetic 

waves absorption characteristics of LBMO. 

 

 

ACKNOWLEDGEMENT 

The authors thank the management of the Center for Science and Technology of Advanced Materials, which has 

provided the research facility. To colleagues in PSTBM especially Dr. Aziz Khan Jahya, thanks for their kind help. 

 

 

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