MICROSTRUCTURAL AND MAGNETIC PROPERTIES OF YTTRIUM …
Transcript of MICROSTRUCTURAL AND MAGNETIC PROPERTIES OF YTTRIUM …
MICROSTRUCTURAL AND MAGNETIC PROPERTIES OF YTTRIUM
IRON GARNET DERIVED FROM STEEL WASTE PRODUCT
NURAINE MARIANA BINTI MOHD SHAHRANI
ITMA 2016 25
© COPYRIG
HT UPM
MICROSTRUCTURAL AND MAGNETIC PROPERTIES OF YTTRIUM
IRON GARNET DERIVED FROM STEEL WASTE PRODUCT
By
NURAINE MARIANA BINTI MOHD SHAHRANI
Thesis submitted to the School of Graduate Studies,
Universiti Putra Malaysia, in Fulfillment of the
Requirement for the Degree of Master of Science
December 2016
© COPYRIG
HT UPM
All materials contained within the thesis, including without limitation text, logos,
icons, photographs and all other artwork, is copyright material of Universiti Putra
Malaysia unless otherwise stated. Use may be made of any material contained
within the thesis for non-commercial purposes from the copyright holder.
Commercial use of material may only be made with the express, prior, written
permission of Universiti Putra Malaysia.
Copyright © Universiti putra Malaysia
© COPYRIG
HT UPM
i
Abstract of thesis presented to the Senate of Universiti Putra Malaysia in
fulfillment of the requirement for the Degree of Master of Science
MICROSTRUCTURAL AND MAGNETIC PROPERTIES OF YTTRIUM
IRON GARNET DERIVED FROM STEEL WASTE PRODUCT
By
NURAINE MARIANA BINTI MOHD SHAHRANI
December 2016
Chairman: Raba’ah Syahidah Azis, PhD
Institute: Institute of Advanced Technology
In this research work, the morphology and magnetic properties-evolutions in Yttrium Iron Garnet (YIG) were studied in details, focusing on parallel evolving
relationship with their dependences on sintering temperature. The iron oxide that
has been used to synthesize YIG was obtained from the steel waste product, mill
scale. There is less study and no reports published regarding the evolution of
microstructure and magnetic properties YIG from low sintering temperature to
high sintering temperature by mill scale waste product. The raw mill scale went
through the milling and purification process by magnetic and non-magnetic
separation and curie temperature separation technique to produce high purity iron
oxide powder as main raw material in preparing YIG and fabricate YIG by high
energy ball milling process. The obtain iron oxide was characterized by X-ray
Diffractometer (XRD), X-ray fluorescence (XRF), X-ray photoelectron
spectroscopy (XPS), Fourier transform infrared spectroscopy (FTIR) and Raman spectroscopy for mineralogical composition and chemical analysis. The results of
XRD indicated that the synthesized iron oxide identified as a α-Fe2O3 (hematite).
Moreover, XRF, XPS, FTIR and Raman data was found to correspond with pure
hematite.
Among the characterization procedures, the highlight properties were phase
identification by XRD, microstructure by FESEM, magnetic permeability by
impedance material analyzer and saturation magnetization by VSM. The XRD
pattern of YIG showed an improvement of crystallinity with increasing sintering
temperature. Full YIG phase was seen for samples sintered at 1100oC and upwards. The temperature obtain of YIG fabricate is comparable with high energy milling
method by commercial iron oxide raw material. FESEM micrographs showed
larger grains as the sintering temperature increased, and the amounts of porosity
were decreased, as the some grains grew at the expense of others. The initial
© COPYRIG
HT UPM
ii
permeability, showed the highest value of 51.70o at 1400oC, and decrement
values of initial permeability at 700oC to 800oC because of the presence of weak
ferromagnetic phases. The results of VSM showed an increasing tendency of
saturation magnetization, with increased grain sizes, and the decrement value
for samples sintering at 700oC to 800oC. These results can be associated with the
formation of weak ferromagnetic behavior of α-Fe2O3 and YFeO3 phases. A
particular pattern of the magnetic properties with sintering temperature is a
manifestation of the phase purity level and microstructural factors. Thus, three
groups of ferromagnetic behavior of YIG can be classified based on those factors.
© COPYRIG
HT UPM
iii
Abstrak tesis yang dikemukakan kepada Senat Universiti Putra Malaysia sebagai
memenuhi keperluan untuk Ijazah Master Sains
MIKROSTRUKTUR DAN SIFAT-SIFAT MAGNET DALAM YTTRIUM
IRON GARNET YANG DIPEROLEHI DARIPADA BAHAN BUANGAN
BESI
Oleh
NURAINE MARIANA BINTI MOHD SHAHRANI
Disember 2016
Pengerusi: Raba’ah Syahidah Azis, PhD
Institut: Teknologi Maju
Dalam kerja-kerja penyelidikan ini, morfologi dan sifat-sifat magnet-evolusi dalam
Yttrium Iron Garnet (YIG) telah dikaji secara terperinci, memberi tumpuan kepada
hubungan perkembangan selari mereka dengan suhu pensinteran. Oksida besi yang
telah digunakan untuk mensintesis YIG diperoleh daripada bahan buangan keluli,
di kilang. Terdapat kurang kajian dan tiada laporan bercetak mengenai evolusi
mikrostruktur dan sifat-sifat magnet YIG dari suhu pensinteran rendah kepada suhu pembakaran tinggi oleh bahan buangan besi dari kilang. Sisik besi mentah telah
melalui proses pengilangan dan pemurnian oleh pemisahan magnet dan bukan
magnet dan teknik pemisahan suhu curie untuk menghasilkan serbuk oksida besi
berketulenan tinggi sebagai bahan mentah utama dalam penyediaan YIG dan
pembuatan YIG oleh proses pengilangan bola tenaga tinggi. Penghasilan oksida
besi telah dicirikan oleh pembelauan sinar-X (XRD), pendarfluor sinar-X (XRF),
spektroskopi fotoelektron sinar-X (XPS), spektroskopi inframerah transform
Fourier (FTIR) dan spektroskopi Raman untuk komposisi mineralogi dan analisis
kimia. Keputusan XRD menunjukkan bahawa oksida besi yang disintesis dikenal
pasti sebagai α-Fe2O3 (bijih besi). Selain itu, data XRF, XPS, FTIR dan Raman
telah didapati sepadan dengan bijih besi tulen.
Di antara prosedur pencirian, sifat-sifat yang diketengahkan adalah pengenalan
fasa oleh XRD, mikrostruktur oleh FESEM, kebolehtelapan magnet oleh
penganalisa bahan galangan dan pemagnetan tepu oleh VSM. Pola XRD daripada
YIG menunjukkan peningkatan penghabluran dengan peningkatan suhu
pensinteran. Fasa YIG penuh dapat dilihat pada sampel sinter pada 1100oC dan ke
atas. Suhu ini adalah setanding dengan kaedah pengilangan bola tenaga tinggi
daripada bahan mentah oksida besi yang komersial. Mikrograf FESEM
© COPYRIG
HT UPM
iv
menunjukkan bijirin lebih besar kerana suhu pembakaran meningkat, dan jumlah
keliangan telah menurun disebabkan oleh beberapa bijirin berkembang sesama
sendiri. Kebolehtelapan awal, menunjukkan nilai tertinggi 51.70o pada suhu
1400oC, dan kebolehtelapan awal susut pada 700
oC dan 800
oC kerana kehadiran
fasa lemah feromagnet. Keputusan VSM menunjukkan pemagnetan tepu, yang
semakin meningkat dengan saiz bijirin meningkat, dan nilai susut pada sampel
pensinteran 700oC dan 800oC. Kesusutan pada suhu ini boleh dikaitkan dengan
pembentukan tingkah laku fasa lemah feromagnet α-Fe2O3 dan YFeO3. Corak
tertentu sifat-sifat magnet dengan pensinteran suhu adalah manifestasi daripada
kesucian tahap fasa dan faktor-faktor mikrostruktur. Maka, tiga kumpulan tingkah laku feromagnet daripada YIG boleh dikelaskan berdasarkan faktor-faktor tersebut.
© COPYRIG
HT UPM
v
ACKNOWLEDGEMENT
First praise is to Allah, the Almighty, on whom ultimately we depend for
sustenance and guidance. With His blessings, help and will, we are able to make
this work a success.
My sincere appreciation and gratitude goes to my supervisor, Dr. Raba’ah
Syahidah Azis for her continuous guidance, advice and support. With her timely
and efficient contribution helped me shape this into its final form and I express my sincerest appreciation for her assistance in any way that I may have asked. I would
also like to extend my appreciation to my supervisory committee member, Assoc.
Prof. Dr. Zulkifly Abbas and Dr. Ismayadi Ismail for their helps throughout this
project.
I gratefully acknowledge the staff of Material Synthesis and Characterization
Laboratory (MSCL), Institute of Advanced Technology, and Faculty of Science for
allowing me to utilize their lab facilities. I would also like to thank Universiti Putra
Malaysia for the financial support by Geran Putra-IPS and Graduate Research
Fellowship Scheme.
A lot of thanks to my colleagues in the Magnetic and Nanostructure Evolution
Group (MNEG), sis Idza Riati Ibrahim, sis Rodziah Nazlan, sis Fadzidah Mohd
Idris, sis Nor Hapishah Abdullah, and sis Wan Norailiana Wan Abdul Rahman for
their concerns, moral support and encouragement. I also appreciate them for the
discussion, ideas and time spent throughout this research. To my fellow friends
during my postgraduate study, Azelah Khairudin and Adilah Zakaria, I would like
to say thanks for everything. Finally, I am forever indebted to my family; parents,
my younger brothers and sisters for their sacrifice, patience, love, understanding,
support and their prayers during these years that I have spent in pursuit of my
master’s degree.
© COPYRIG
HT UPM
© COPYRIG
HT UPM
vii
This thesis was submitted to the Senate of Universiti Putra Malaysia and has been
accepted as fulfillment of the requirement for the degree of Master of Science. The
members of the Supervisory Committee were as follows:
Rabaah Syahidah binti Azis, PhD
Senior Lecturer
Faculty of Science
Universiti Putra Malaysia
(Chairman)
Zulkifly bin Abbas, PhD
Associate Professor
Faculty of Science
Universiti Putra Malaysia
(Member)
Ismayadi bin Ismail, PhD
Fellow Researcher
Institute of Advanced Technology
Universiti Putra Malaysia
(Member)
ROBIAH BINTI YUNUS, PhD
Professor and Dean
School of Graduate Studies
Universiti Putra Malaysia
Date:
© COPYRIG
HT UPM
viii
Declaration by graduate student
I hereby confirm that:
this thesis is my original work;
quotations, illustrations and citations have been duly referenced;
this thesis has not been submitted previously or concurrently for any other
degree at any other institutions;
intellectual property from the thesis and copyright of thesis are fully-
owned by Universiti Putra Malaysia, as according to the Universiti Putra
Malaysia (Research) Rules 2012;
written permission must be obtained from supervisor and the office of Deputy Vice-Chancellor (Research and Innovation) before thesis is
published (in the form of written, printed or in electronic form) including
books, journals, modules, proceedings, popular writings, seminar papers,
manuscripts, posters, reports, lecture notes, learning modules or any other
materials as stated in the Universiti Putra Malaysia (Research) Rules
2012;
there is no plagiarism or data falsification/fabrication in the thesis, and
scholarly integrity is upheld as according to the Universiti Putra Malaysia
(Graduate Studies) Rules 2003 (Revision 2012-2013) and the Universiti
Putra Malaysia (Research) Rules 2012. The thesis has undergone
plagiarism detection software.
Signature: _______________________ Date: __________________
Name and Matric No.: _________________________________________
© COPYRIG
HT UPM
ix
Declaration by Members of Supervisory Committee
This is to confirm that:
the research conducted and the writing of this thesis was under our supervision;
supervision responsibilities as stated in the Universiti Putra
Malaysia (Graduate Studies) Rules 2003 (Revision 2012-
2013) are adhered to:
Signature: _________________ Name of
Chairman of Supervisory
Committee: ________________
Signature: _________________
Name of
Member of Supervisory
Committee: ________________
Signature: _________________
Name of
Member of Supervisory
Committee: ________________
© COPYRIG
HT UPM
x
TABLE OF CONTENTS
Page
ABSTRACT Ii i
ABSTRAK iii
ACKNOWLEDGEMENTS v
APPROVAL vi
DECLARATION viii
LIST OF TABLES xiii
LIST OF FIGURES xiv
LIST OF SYMBOLS AND ABBREVIATIONS xvii
CHAPTER
1 INTRODUCTION 1
1.1 Background of study 1
1.2 Magnetic ceramics 2
1.3 Introduction of Garnets 2
1.4 Mill scale as a potential of raw materials 2
1.5 Aim of study 4
1.6 Objectives 4
2 LITERATURE REVIEW 5 2.1 Introduction 5
2.2 Processing technique of Iron oxide using mill scale waste
product
5
2.3 Processing of YIG 6
2.3.1 Mixed oxides method 6
2.3.2 Coprecipitation 7
2.3.3 Sol-gel synthesis 8
2.3.4 Mechanical milling 9
2.4 Magnetic and electrical properties of garnet 10
2.4.1 Oxygen stoichiometry 11
2.5 Microwave properties of garnet 12
2.6 Microstructural dependence on magnetic properties of garnet
14
2.6.1 Effect of grain size on permeability 14
2.6.2 Effect of porosity on permeability 15
2.6.3 Effect of grain size and porosity on M-H
parameters
15
2.6.4 Imperfections 16
2.7 Microstructural dependence on microwave properties 16
3 THEORY 17
3.1 Introduction 17
3.2 Origin of magnetism 17 3.2.1 Ferrimagnetism 17
3.3 Superexchange interaction of YIG 19
3.4 Magnetic properties of ferromagnetic materials 21
3.4.1 Magnetic domains and Bloch walls 21
© COPYRIG
HT UPM
xi
3.4.1.1 Magnetostatic energy 23
3.4.1.2 Magnetocrystalline energy 23
3.4.1.3 Magnetostrictive energy 23
3.4.1.4 Domain wall energy 24
3.4.2 Saturation magnetization 24
3.4.3 Curie temperature 25
3.4.4 Magnetic anisotropy 26
3.4.5 M-H hysteresis curve 27
3.4.6 Magnetic losses 29
3.4.7 Resistivity 30
3.4.8 Permeability 31 3.5 Magnetic properties of garnets 33
3.6 Significance of high temperature 33
3.7 High energy ball milling method 34
3.7.1 Mechanism of high energy ball milling 35
3.8 Influence of temperature on microstructure and magnetic
properties
35
4 METHODOLOGY 37
4.1 Introduction 37
4.2 Preparation of hematite, Fe2O3 37
4.2.1 Selecting raw materials 39 4.2.2 Weighing and blending 39
4.2.3 Separation techniques 39
4.2.3.1 Magnetic and non-magnetic (MNM) 40
4.2.3.2 Curie temperature separation (CTS) 40
4.2.4 Fe2O3 production 41
4.3 Preparation of YIG 41
4.3.1 Powder preparation 42
4.3.2 Compact formation 43
4.3.3 Sintering 43
4.4 Sample measurement and characterization 44
4.4.1 Particle size analysis 45
4.4.2 Phase analysis 45 4.4.3 Microstructure analysis 45
4.4.4 Density measurement 46
4.4.5 Measurement of magnetization 46
4.4.6 Measurement of complex permeability 47
4.4.7 Measurement of curie temperature 47
4.4.8 Measurement of electrical resistivity 48
4.4.9 Structural analysis by FTIR spectroscopy 49
4.4.10 Structural analysis by Raman spectroscopy 49
4.4.11 Elemental composition by XRF spectroscopy 50
4.4.12 Elemental composition by XPS 50
4.4.13 Linewidth 50 4.5 Flowchart of characterization of YIG by mill scale 51
5 RESULTS AND DISCUSSION 53
5.1 Introduction 53
© COPYRIG
HT UPM
xii
5.2 Hematite characterization 53
5.2.1 Phase analysis 53
5.2.2 Elemental composition by XRF 55
5.2.3 Structural analysis by FTIR 56
5.2.4 Structural analysis by Raman 57
5.2.5 Elemental composition by XPS 59
5.3 YIG Characterization 62
5.3.1 Phase analysis 62
5.3.2 Structural analysis by FTIR 68
5.3.3 Structural analysis by Raman 69
5.3.4 Microstructural related analysis 70 5.3.4.1 Particle size 70
5.3.4.2 Morphology, grain size and porosity 71
5.3.5 Magnetic properties 78
5.3.5.1 Saturation magnetization and coercivity 78
5.3.5.2 Complex permeability 84
5.3.5.3 Curie temperature 84
5.3.6 Electrical resistivity 89
5.3.7 Linewidth 91
5.4 Summary 92
6 CONCLUSION AND SUGGESTIONS 95 6.1 Conclusion 95
6.2 Summary 96
6.3 Recommendations for further studies 98
REFERENCES 99
APPENDICES 104
BIODATA OF STUDENT 108
LIST OF PUBLICATIONS 109
© COPYRIG
HT UPM
xiii
LIST OF TABLES
Table Page
3.1 Classes of magnetic ceramics. 19
3.2 The angle of yttrium-oxygen-iron and iron-oxygen-iron
linkages in YIG.
20
4.1 General properties of hematite, magnetite and wustite. 41
5.1 Parameters composition, chemical formula, crystal system,
space group, density x-ray (Dx), lattice parameters for (a)
mill scales, (b) after CTS and (c) after oxidation process.
55
5.2 Elemental composition of raw mill scale. 56
5.3 Elemental composition of hematite. 56
5.4 Raman wavenumbers and assignments of hematite compared
with values reported in the literature.
58
5.5 Binding energies in eV of major core lines in iron oxide,
hematite.
62
5.6 XRD details of the intense peaks before sintering (after 9
hours milling) and at sintering temperature 500oC to 1400oC.
65
5.7 Volume fraction of phases at sintering temperature 500oC to
1400oC.
66
5.8 Average grain sizes at sintering temperature 500oC to
1400oC.
72
5.9 Density, relative density and porosity at sintering
temperature 500oC to 1400oC.
78
5.10 Saturation magnetization at sintering temperature 500oC to
1400oC.
81
5.11 Initial permeability at sintering temperature 500oC to
1400oC.
88
5.12 Curie temperature at sintering temperature 500oC to 1400oC. 89 5.13 Resistivity at sintering temperature 500oC to 1400oC. 90
5.14 Linewidth at sintering temperature 500oC to 1400oC
measured at the frequency of 4-8 GHz.
91
5.15 Relationship of sintering temperature with volume fraction
of phases, bulk density db, porosity P, grain sizes D,
saturation magnetization Ms, coercivity Hc, initial
permeability µi, Curie temperature Tc, resistivity and
linewidth ΔH.
94
© COPYRIG
HT UPM
xiv
LIST OF FIGURES
Figure Page
2.1 Phase diagram of the system Fe2O3-Y2O3 in air. 12
2.2 Linewidth, and dielectric loss tangent, tan measured
at 10 GHz as a function of initial iron defect for a material having the formula Y3Fe5(1-ε)O12.
13
2.3 Linewidth, ΔH versus temperature for two YIG’s which
have the following densities: (1) d1 = 5.151 g/cm3, (2) d2 =
5.128 g/cm3.
14
3.1 Schematic comparing dipole allignments in ferromagnetic,
antiferromagnetic and ferrimagnetic materials in A and B
sites.
18
3.2 The coordination of Y3+ ion in 24(c), Fe3+ ion in 16(a) and
Fe3+
ion in 24(d) with oxygen ion in YIG.
20
3.3 Schematic representation of the domains in a ferromagnetic; arrows represent atomic magnetic dipoles.
Within each domain, all dipoles are aligned, whereas the
direction of alignment varies from one domain to another.
22
3.4 Gradual change in direction of moments inside a domain
wall.
22
3.5 M-H curve. 25
3.6 The - behavior for a ferromagnetic material that was
initially unmagnetized. Domain configurations during
several
stages of magnetization are represented.
28
3.7 The - for a ferromagnetic material that is subjected to forward and reverse saturation.
29
3.8 Permeability spectrum of a YIG showing the frequency
course of the real and imaginary permeabilities.
32
3.9 Coercivity as a function of particle size. 36
4.1 Flowchart of Fe2O3 preparation from mill scale. 38
4.2 Separation set-up of MNM and CTS. 40
4.3 Flowchart of YIG preparation. 42
4.4 Illustration of a (a) pellet and (b) toroidal shape sample. 43
4.5 Density measurement set-up. 46
4.6 Air mill that used for making spherical shape sample. 47 4.7 Curie temperature measurement set-up. 48
4.8 Electrical resistivity measurement set-up. 49
4.9 Linewidth measurement set-up. 51
4.10 Flowchart of YIG bulk ferrite characterization. 52
5.1 XRD pattern of (a) mill scale, (b) mill scale after curie
separation technique (CTS) and (c) after oxidation process.
54
5.2 FTIR spectrum of hematite from mill scale. 57
5.3 Raman spectrum of hematite. 58
5.4 XPS response of full survey of iron oxide, hematite. 60
© COPYRIG
HT UPM
xv
5.5 Fe 2p3/2 and Fe 2p1/2 position of iron oxide, hematite. 60
5.6 Fe 3p and Fe 3s position of iron oxide, hematite. 61
5.7 The O 1s position of iron oxide, hematite. 62
5.8 XRD pattern of Fe2O3 + Y2O3 mixture milled at 9 hours and
sintered at different temperature (from 500oC to 1400oC)
for 9 hours.
64
5.9 Approximate comparison of percentage amorphous grain
boundary volumes in YIG with nanometer and micrometer
grain size.
67
5.10 FTIR spectra at sintering temperature 500oC to 1400oC. 69
5.11 Raman spectra at sintering temperature 500oC to 1400oC. 70 5.12(a) TEM image of the powder milled for 9 hours. 71
5.12(b) Particle size distribution of the powder milled for 9 hours. 71
5.13 FESEM micrograph at 500oC, 600oC, 700oC, 800oC, 900oC,
1000oC, 1100oC, 1200oC, 1300oC and 1400oC.
74
5.14 Grain size distribution at 500oC, 600oC, 700oC, 800oC,
900oC, 1000
oC, 1100
oC, 1200
oC, 1300
oC and 1400
oC.
76
5.15 Magnetization curve at sintering temperature 500oC to
1400oC.
79
5.15(a) Magnetization curve at sintering temperature 500oC to
800oC.
80
5.15(b) Magnetization curve at sintering temperature 900oC to
1400oC.
80
5.16(a) Saturation magnetization relationship with grain size as
increasing sintering temperature.
82
5.16(b) Coercivity relationship with grain sizes as increasing
sintering temperature.
83
5.17 Coercivity and morphology at sintering temperature 500oC
to 1400oC.
83
5.18 Real permeability at sintering temperature 500oC to
1400oC.
85
5.18(a) Real permeability at sintering temperature 500oC to 800oC. 85
5.18(b) Real permeability at sintering temperature 900oC to
1400oC.
86
5.19 Permeability loss factor at sintering temperature 500oC to
1400oC.
86
5.19(a) Permeability loss factor at sintering temperature 500oC to
800oC.
87
5.19(b) Permeability loss factor at sintering temperature 900oC to
1400oC.
87
5.20 Curie temperature at sintering temperature 500oC to
1400oC.
89
5.21 Resistivity at sintering temperature 500oC to 1400oC
Measured at room temperature.
90
© COPYRIG
HT UPM
xvi
5.22 Linewidth at sintering temperature 500oC to 1400oC
measured at the frequency of 4-8 GHz.
92
© COPYRIG
HT UPM
xvii
LIST OF SYMBOLS AND ABBREVIATIONS
Ni Nickel
Mn Manganese
Zn Zinc
Ba Barium
Sr Strontium Fe2O3 Iron (III) oxide; hematite
Y2O3 Yttrium oxide
Y3Fe5O12; YIG Yttrium iron garnet
Y Yttrium
FeO Iron (II) oxide
Fe3O4 Iron (II,III) oxide
Fe Iron
CTS Curie temperature separation
MNM Magnetic and non-magnetic separation
XRF X-ray fluorescence
XRD X-ray diffraction
Cu Copper Cr Chromium
YFeO3; YIP Orthoferrite
FMR Ferromagnetic resonance
ΔH Linewidth
Fe3+ Iron (III) ion; ferric ion
Fe2+ Iron (II) ion; ferrous ion
Hc Coercivity
Mr Remanence
M Magnetization
Tc Curie temperature
Ms Saturation magnetization H Applied field
Ρ Resistivity
HEBM High energy ball milling
FTIR Fourier transform Infrared spectroscopy
XPS X-ray photoelectron spectroscopy
µ’ permeability
µi Initial permeability
µ’’ Permeability loss factor
µB Bohr magneton
m Magnetic moment
Ca Calcium V Vanadium
Sn Tin
K Anisotropy
DC Direct current
AC Alternating current
VSM Vibrating sample magnetometer
© COPYRIG
HT UPM
xviii
FESEM Field emission scanning electron
microscope
a-sublattice Octahedral sublattice
d-sublattice Tetrahedral sublattice
c-sublattice Dodecahedral sublattice
D Grain size
R Resistance
P Porosity
db Bulk density
© COPYRIG
HT UPM
1
CHAPTER 1
INTRODUCTION
1.1 Background of study
Oxide ceramics which exhibit ferrimagnetic behavior play an important role in the
electronic industry. They are commonly known as ferrites. Ferrites are the mixed metal oxides containing iron oxide as their main component. There are three
important classes of commercial ferrites, and each of one having a specific crystal
structure. The first one is soft ferrites with cubic spinel structure, such as NiZn-
and MnZn ferrites. The second one is the soft ferrites with garnet structure, such as
the microwave ferrites, for example yttrium iron garnet, and the third one is hard
ferrites with the hexagonal structure such as Ba and Sr hexaferrites. The industrial
importance of ferrites becomes obvious when one examines the diversity of their
applications. Through the years, the demand of ferrites has steadily increased
together with the specific applications of ferrites, and have changed remarkably
and kept pace with the development in electronic technologies.
Ceramic technology has historically developed from an empirical method of
fabrication to one which is based more and more on the application of scientific
knowledge. It has become quite evident that the parameters determining the
suitability of materials for particular applications are chemical composition,
crystallographic structure and the so-called microstructure, which comprises such
important aspects as size of constituent crystallites (grains), their size distributions,
their boundaries (grain boundaries), their orientation (texture), and the voids
(pores) between them (Sun, 2007). To control and manipulate these parameters,
there must be a range of methods available for preparing ceramic powders. There
are three basic methods, which are mechanical, chemical, and vapor phase
methods.
Mechanical methods use coarse-grained materials which is often necessary to
eliminate aggregates and to reduce particle size. They are subjected to a series of
processes called as comminution. The steps involved crushing, grinding, and
milling. Mechanical methods of powder production are widely used in the industry
due to ability for high mass production of the product. Chemical methods such as
sol-gel processing offer several advantages over mechanical methods. This method
allows exceptional control over particle morphology and purity at lower
temperatures. Chemical processes are widely used in the production of advanced
ceramic materials such as fibers, coatings, etc. (Cheng et al., 2007). The other method is vapor-phase processes. Vapor-phase processes offer many advantages,
such as the ability to produce particles of non-oxides and nanoparticles, as they can
give high purity powders, discrete and non-aggregated particles, and nanoparticles
with narrow size distributions (Guo et al., 2005).
© COPYRIG
HT UPM
2
In this chapter, the general information on ferrite magnetic garnets is introduced.
An introduction on raw steel waste (well-known as mill scale) and its potential in
producing iron oxide powder will be highlighted. In the thesis, we will discuss the
previous work on the synthesis compound within the Fe2O3-Y2O3 system by
mechanical alloying method and the statistical analysis data by this method.
Theories that are related with the results are also discussed. The materials used and
the procedure of the research will be compile followed with the results and
discussion. Based on the results, we will summarize and conclude the research
findings, in addition to some suggested recommendations for future work.
1.2 Magnetic ceramics
In recent years, ferrimagnetic garnet have attracted much attention as microwave
device materials, circulators, isolators, phase shifters, etc. due to its excellent
electromagnetic properties, including low dielectric loss, narrow ferromagnetic
resonance linewidth in microwave region and tailorable saturation magnetization
(Yu et al., 2011). Thus, research has been committed to the investigations of YIG
and doped-YIG by controlling the preparation conditions to tailor their
microstructure in addition to the design of chemical composition.
1.3 Introduction of Garnets
Generally, the chemical formula for garnet system is written as 3M2O3.5Fe2O3 or
M3Fe5O12. M represents yttrium (Y) or one of the rare earth ions. The rare earth
ions are large, so that they occupy the largest cation sites in the garnet structure,
which are dodecahedral sites. Note that in the magnetic garnet, the metal ions are
all trivalent. There are 24 dodecahedral, 16 octahedral, and 24 tetrahedral sites in a
unit cell containing 8 formula units. The prototype for ferrimagnetic iron garnet is
yttrium iron garnet (YIG). Garnets provide superior performance in microwave
devices because they have narrow resonance line width, one of the most important parameters from application point of view besides wide range of magnetization and
very low dielectric loss (Soleimani et al., 2012).
1.4 Mill scale as a potential of raw materials
The processes of manufacturing steel product from industry produce two times
more waste materials than the final product obtained. These results in the
formation of large amounts of waste materials in the form of slags, scale and dusts
(Martin et al., 2012). Currently, most of the waste is utilized in the same steelworks and passed to external customers or it is reused as a feeds for other technological
processes. In the case of Malaysia’s steel Industry, Malaysia’s consumption on
steel is expected to trend up along with on-going construction and mass transit
projects. The demand of steel is expected to rise up by 12.6% year-of-year (Export-
© COPYRIG
HT UPM
3
Import Bank of Malaysia, 2015). In 2013, 11.69% million tons of steels are
produced and increased to 12.5% million tons in 2014 (“World Steel Association,”
2014). This trend is expected to increase up in year 2020. The steel industry in
Malaysia can be categorically subdivided into two main segments, namely long
products and flat products. Long products include billets, bars, wire rods, sections,
nails, wire mesh, nuts, bolts, etc. which are predominantly used in the construction
industry. Flat products are the products consumed mostly by the manufacturing,
construction and oil & gas sectors like hot-rolled plates and sheets, cold-rolled
coils, tubes, pipes, boiler and pressure vessels, etc. Irrespective of the products,
during processing of steel to yield long or flat product, mill scale is generated and
considered as a waste (Bagatini et al., 2011).
Mill scale is flaky that can be found on metals that have been rolled. Mill scale
forms an exterior surface of sheets and plates as they are being manufactured
through rolling steel billets and hot iron into rolling mills. Mill scale which
represents 2% of steel produced contains iron in elemental form and three types of
iron oxides: wustite (FeO), hematite (α-Fe2O3) and magnetite (Fe3O4) (Legodi and
de Waal, 2007). The chemical composition of mill scale depends on the type of
steel produced and the process used. The iron content in the mill scale is normally
around 72% Fe with small amounts of non-ferrous metals. Mill scale is
contaminated with remains of lubricants and other oils and greases from the equipment associated with rolling operations (Martin et al., 2012). The oil content
usually ranges between 0.1 % and 2.0%, and can reach up to 10.0%. In steelworks
plants, almost 85% of the mill scale generated is recycled within the steelmaking
industry and small amounts are used for ferroalloys, in cement plants and in the
petrochemicals industry. The balance part of the mill scale with particle size less
than 0.5 mm (finer mill scale or mill scale sludge), which is more heavily
contaminated with oils, ends up in landfills. Mill scale sludge cannot be recycled
via sintering since its fine particles contains a high oil level which is 5.0-20.0% and
is normally treated as a landfill waste. Mill scale with oil content more than 3.0%
is recycled after extracting the oil in a pre-treatment stage. Mill scale with oil
content less than 1.0% with the particle size between 0.5-5.0 mm can be returned
without any pre-treatment (Legodi and de Waal, 2007). Thus, the allowable limit for oil content in the mill scale is less than 1% for all usage.
Although most of the mill scales are consumed after recycling, and only small
amounts are used in ferroalloys, cement and petrochemicals industry, there is a
potential for production of steel increase up to 1.0 million tons with the increase in
construction activities, current economic needs in emerging markets and growing
concern over the use of steel in heavy industries. All the above gives an initiative
to find suitable means for effective utilization of mill scale and a low cost by-
product in the steelmaking industry. In the present research, we have employed the
mill scale waste product from the Malaysian steel factories. The steel are collected from Perwaja Steel Terengganu. The immense amount of steel waste give a
challenge for us to extract the iron oxide contained in the mill scale by a
purification technique and producing iron oxide for magnetic materials.
© COPYRIG
HT UPM
4
1.5 Aim of study
In several past decades, studies on YIG by pure materials are reported in ferrite
literature. Instead, fabrication of YIG ferrite by using recycled steel waste product
(mill scale) is still investigated. There are no reports from literature on this work.
Steel waste products are collected from steel industry in Malaysia. It has high
content of iron (Fe) and gives us a challenge to purify and recycled the powder to
produce YIG ferrites. This project will highlight the low cost ferrite fabrication
from the waste material.
Ferrite magnetic materials are known very rely to their microstructure. Nowadays,
the fundamental on scientific enquiry of the microstructure-property evolution has
been neglected. Therefore, in this work, the evolutions of the microstructure-
magnetic properties relationship at various sintering temperature on the
morphology and material properties will be investigated.
1.6 Objectives
The interest of this research is to track down the parallel evolution of
microstructural and magnetic properties from lower sintering temperature (500oC)
to higher temperature (1400oC) of YIG. Hence, the study embarks on the following
objectives:
I. To purify recycled mill scale waste product by magnetic and non-
magnetic separation (MNM) and Curie temperature separation technique
(CTS) collected from steel industries in Malaysia to produce high purity
Fe2O3 as main raw materials in fabrication YIG ferrite by using
mechanical alloying technique.
II. To elucidate the parallel evolution of the magnetic properties with microstructural changes and their relationship in nano-micro yttrium iron
garnet ferrites at various sintering temperatures.
© COPYRIG
HT UPM
99
REFERENCES
Anderson, E. E. (1946). Ferromagnetic Insulators: Garnets. In E. P. Wohlfarth
(Ed.), Ferromagnetic Materials (pp. 26). Amsterdam, NY: North-Holland.
Anderson, P. W. (1950). Ferrites for Non-Microwave Applications. In E. P.
Wohlfarth (Ed.), Ferromagnetic Materials (pp. 202). Amsterdam, NY:
North-Holland.
Azis, R. S., Hashim, M., Saiden, N. M., Daud, N., & Shahrani, N. M. M. (2015).
Study the iron environments of the steel waste product and its possible
potential applications in ferrites. Advanced Materials Research, 1109, 295–99.
Azis, R. S., Hashim, M., Zakaria, A., Hassan, J., Daud, N., Shahrani, N. M. M., &
Siang, P. C. (2016). Magnetic properties and microstructures of cobalt
substituted barium Hexaferrites derived from steel waste product via
mechanical alloying technique. Material Science Forum, 846, 388–94.
Badwal, S. P. S., & Drennan, J. (1987). Yttria-zirconia: Effect of microstructure on
conductivity. Journal of Materials Science, 22(9), 3231–39.
Bagatini, M. C., Zymla, V., Osório, E., & Vilela, A. C. F. (2011). Characterization
and Reduction Behavior of Mill Scale. ISIJ International, 51(7), 1072–79.
Cao, W. (n.d.). Synthesis of nanomaterials by high energy ball milling. Retrieved
from http://www.ssnano.com. Chamritski, I., & Burns, G. (2005). Infrared- and Raman-active phonons of
magnetite, maghemite, and hematite: A Computer Simulation and
Spectroscopic Study. Journal of Physical Chemistry B, 109(11), 4965–68.
Cheng, Z., Yang, H., Cui, Y., Yu, L., Zhao, X., & Feng, S. (2007). Synthesis and
Magnetic Properties of Y3-xDyxFe5O12 nanoparticles. Journal of Magnetism
and Magnetic Materials, 308(1), 5–9.
Chiu, W. S., Radiman, S., Abd-Shukor, R., Abdullah, M. H., & Khiew, P. S.
(2008). Tunable coercivity of CoFe2O4 nanoparticles via thermal annealing
treatment. Journal of Alloys and Compounds, 459, 291–297.
Daud, N., Azis, R. S., Hashim, M., Matori, K. A., Hassan, J., Saiden, N. M., &
Shahrani, N. M. M. (2016). Preparation and characterization of Sr1-
xNdxFe12O19 derived from steel-waste product via mechanical alloying. Materials Science Forum, 846, 403–9.
de Faria, D. L. A., Silva, S. V., & de Oliveira, M. T. (1997). Raman
microspectroscopy of some iron oxides and oxyhydroxides. Journal of
Raman Spectroscopy, 28, 873–878.
Epstein, D. J., Anantha, N. G., Hunt, R. P., Janak, J. F., Frackiewicz, B., Kelly, W.
F., Lovell, B. W., Mac Millan, A. J., & Judy, J. J. (1962). Magnetic loss
phenomena in ferromagnetic materials (Report No. AF 19(604)-5482).
Retrieved from Massachusetts Institute of Technology for Research in
Electronics website: http://www.dtic.mill/dtic.
Export-Import Bank of Malaysia Berhad. (2015). Summary of Iron & Steel
Industry. Retrieved from http://www.exim.com.my/media-centre/advisory-research/industry-assessment/summary-iron-steel-industry-malaysia.
Fernandez-Garcia, L., Suarez, M., & Menendez, J. L. (2010). Synthesis of mono
and multidomain YIG particles by chemical coprecipitation or ceramic
procedure. Journal of Alloys and Compounds, 495(1), 196–199.
© COPYRIG
HT UPM
100
Geller, S., & Gilleo, M. A. (1957). Ferromagnetic Insulators: Garnets. In E. P.
Wohlfarth (Ed.), Ferromagnetic Materials (pp. 20). Amsterdam, NY: North-
Holland.
Gilleo, M. A., & Geller, S. (1958). Ferromagnetic Insulators: Garnets. In E. P.
Wohlfarth (Ed.), Ferromagnetic Materials (pp. 21). Amsterdam, NY: North-
Holland.
Gleiter, H. (1989). Nanocrystalline Materials. Progress in Materials Science,
33(4), 223–315.
Globus, A., & Guyot, M. (1972). Wall displacement and bulging in magnetization
mechanisms of the hysteresis loop. Physica Status Solidi (b), 52(2), 427-431.
Guo, X.Z., Ravi, B. G., Devi, P. S., Hanson J. C., Margolies, J., Gambino, R. J., Parise, J. B., & Sampath, S. (2005). Synthesis of Yttrium Iron Garnet (YIG)
by citrate–nitrate gel combustion and precursor plasma spray processes.
Journal of Magnetism and Magnetic Materials, 295, 145–154.
Hanesch, M. (2009). Raman spectroscopy of iron oxides and (oxy)hydroxides at
low laser power and possible applications in environmental magnetic studies.
Geophysical Journal International, 177, 941–948.
Heister, W. (1959). Magnetic properties and grain structure of Mn-Zn ferrites.
Journal of Applied Physics, 30(4), 22–24.
Holmquist, W. R., Kooi, C. F., & Moss, R. W. (1961). Reaction kinetics of
polycrystalline Yttrium Iron Garnet. Journal of the American Ceramic
Society, 44(4), 194–196. Huang, H., Gong, H., Tang, D., & Tan, O. K. (2009). Synthesis and
characterization of Yttrium Aluminum Garnet by high-energy ball milling.
Optical Materials, 31, 716–719.
Idza, I. R., Hashim, M., Rodziah, N., Ismayadi, I., & Norailiana, A. R. (2012).
Influence of evolving microstructure on magnetic-hysteresis characteristics
in polycrystalline nickel-zinc ferrite, Ni0.3Zn0.7Fe2O4. Materials Research
Bulletin, 47, 1345–1352.
Igarashi, H., & Okazaki, K. (1977). Effects of porosity and grain size on the
magnetic properties of NiZn ferrite. Journal of the American Ceramic
Society, 60(1–2), 51–54.
Jordan, H. (1924). Ferrites for Non-Microwave Applications. In E. P. Wohlfarth
(Ed.), Ferromagnetic Materials (pp. 221). Amsterdam, NY: North-Holland. Joseyphus, R. J., Narayanasamy, A., Nigam, A. K., & Krishnan, R. (2006). Effect
of mechanical milling on the magnetic properties of garnets. Journal of
Magnetism and Magnetic Materials, 296, 57–64.
Kittel, C. (1956). Theory of the structure of ferromagnetic domains in films and
small particles. Physical Review, 70(11-12), 965–971.
Koelberer, R. E., & Patton, C. E. (1977). Microwave Ferrites. In E. P. Wohlfarth
(Ed.), Ferromagnetic Materials (pp. 259). Amsterdam, NY: North-Holland.
Kramers, H. A. (1934). Ferromagnetic Insulators: Garnets. In E. P. Wohlfarth
(Ed.), Ferromagnetic Materials (pp. 20). Amsterdem, NY: North-Holland.
Legodi, M. A., & de Waal, D. (2007). The Preparation of magnetite, goethite,
hematite and maghemite of pigment quality from mill scale iron waste. Dyes and Pigments, 74(1), 161-168.
Li, Y-S., Church, J. S., & Woodhead, A. L. (2012). Infrared and raman
spectroscopic studies on iron oxide magnetic nano-particles and their surface
modifications. Journal of Magnetism and Magnetic Materials, 324, 1543–
© COPYRIG
HT UPM
101
1550.
Martín, M. I., López, F. A., & Torralba, J. M. (2012). Production of sponge iron
powder by reduction of rolling mill scale. Ironmaking & Steelmaking, 39(3),
155–62.
McIntyre, N. S., & Zetaruk, D. G. (1977). X-Ray Photoelectron Spectroscopic
Studies of Iron Oxides, Analytical Chemistry, 49(11), 1521–1529.
Mergen, A., & Qureshi, A. (2009). Characterization of YIG nanopowders by
mechanochemical synthesis. Journal of Alloys and Compounds, 478, 741–
744.
Mills, P., & Sullivan, J. L. (1983). A study of the core level electrons in iron and its
three oxides by means of x-ray photoelectron spectroscopy. Journal of Physics D: Applied Physics, 16(5), 723-732.
Minghao, F., Juntong, H., Zhaohui, H., Yangai, L., Bin, J., & Peng, P. (2008).
Solid phase synthesis and sintering properties of Yttrium Iron Garnet. Key
Engineering Materials, 368-372, 588–590.
Nazlan, R., Hashim, M., Abdullah, N. P., Ibrahim, I. R., & Ismail, I. (2012).
Influence of milling time on the crystallization, morphology and magnetic
properties of polycrystalline Yttrium Iron Garnet. Advanced Materials
Research, 501, 324–328.
Nazlan, R., Hashim, M., Ibrahim, I. R., & Ismail, I. (2014). Dependence of
magnetic hysteresis on evolving single-sample sintering in fine-grained
Yttrium Iron Garnet. Journal of Superconductivity and Novel Magnetism, 27(2), 631–39.
Neel, L. (1948). Ferrites for Non-Microwave Applications. In E. P. Wohlfarth
(Ed.), Ferromagnetic Materials (pp. 202). Amsterdam, NY: North-Holland.
Nielsen, J. W., & Dearborn, E. F. (1958). The growth of single crystals of magnetic
garnets. Journal of Physics and Chemistry of Solids, 5, 202–207.
Oh, S. J., Cook, D. C. & Townsend, H. E. (1998). Characterization of iron oxides
commonly formed as corrosion products on steel. Hyperfine Interact,112,
59–65.
Otsuki, T. (1992). Modern Ferrite Technology. Dordrecht, Netherland: Kluwer
Academic
Paesano, A., Zanatta, S. C., De Medeiros, S. N., Cótica, L. F., & Da Cunha, J. B.
M. (2005). Mechanosynthesis of YIG and GdIG: A structural and mössbauer study. Hyperfine Interactions, 161, 211–20.
Paladino, A. E., & Maguire, E. A. (1970). Microstructure development in Yttrium
Iron Garnet. Journal of the American Ceramic Society, 53(2), 98–102.
Patton, C. E. (1970). Effect of grain size on the microwave properties of
polycrystalline Yttrium Iron Garnet. Journal of Applied Physics, 41(4),
1637–1641.
Pauthenet, R. (1958). Ferromagnetic Insulators. In E. P. Wohlfarth (Ed.),
Ferromagnetic Materials (pp. 26). Amsterdam, NY: North-Holland.
Prince, E. (1957). Ferromagnetic Insulators: Garnets. In E. P. Wohlfarth (Ed.),
Ferromagnetic Materials (pp. 8). Amsterdam, NY: North-Holland.
Ristic, M., Nowik, I., Popovic, S., Felner, I., & Music, S. (2003). Influence of synthesis procedure on the YIG formation. Materials Letters, 57, 2584–2590.
Sánchez-De Jesús, F., Cortés, C. A., Valenzuela, R., Ammar, S., & Bolarín-Miró,
A. M. (2012). Synthesis of Y3Fe5O12 (YIG) assisted by high-energy ball
milling. Ceramics International, 38, 5257–5263.
© COPYRIG
HT UPM
102
Singh, K. K., & Bhattacharjee, S. (2007). Study on the effect of high energy ball
milling (a nano material process) on the microstructure and mechanical
properties of a (Al-Si-Fe-Cu) alloy study (Degree's thesis, National Institute
of Technology Rourkela). Retrieved from http://www.ethesis.nitrkl.ac.in.
Slick, P. I. (1971). Ferrites for Non-Microwave Applications. In E. P. Wohlfarth
(Ed.), Ferromagnetic Materials (pp. 202). Amsterdem, NY: North-Holland.
Soleimani, H., Abbas, Z., Yahya, N., Shameli, K., Soleimani, H., & Shabanzadeh,
P. (2012). Reflection and transmission coefficient of Yttrium Iron Garnet
filled polyvinylidene fluoride composite using rectangular waveguide at
microwave frequencies. International Journal of Molecular Sciences, 13,
8540–8548. Stoops, R. F., & Hamme, J. V. (1964). Phase relations in the system uranium-
carbon-oxygen. Journal of the American Ceramic Society, 47(2), 59–62.
Sun, C. Q. (2007). Size dependence of nanostructures: Impact of bond order
deficiency. Progress in Solid State Chemistry, 35, 1–159.
Sztaniszlav, A., Sterk, E., & Fetter, L. (1984). Investigation of garnet formation by
sintering of Y2O3 and Fe2O3. Journal of Magnetism and Magnetic Materials,
41, 75–78.
Van Hook, H. J. (1961). Phase relations in the system Fe2O3-Fe3O4-YFeO3 in air.
Journal of the American Ceramic Society, 44(5), 208–214.
Vaqueiro, P., Crosnier-Lopez, M. P. & Lopez-Quintela, M. A. (1996). Synthesis
and characterization of Yttrium Iron Garnet nanoparticles. Journal of Solid State Chemistry, 126, 161–168.
Vaqueiro, P., Lopez-Quintela, M. A., Rivas, J., & Greneche, J. M. (1997).
Annealing dependence of magnetic properties in nanostructured particles of
Yttrium Iron Garnet prepared by citrate gel process. Journal of Magnetism
and Magnetic Materials, 169, 56–68.
Veitch, C. D. (1991). Synthesis of polycrystalline Yttrium Iron Garnet and Yttrium
Aluminium Garnet from organic precursors. Journal of Material Science,
26(23), 6527–6532.
Wang, H., Gao, L., & Niihara, K. (2000). Synthesis of nanoscaled Yttrium
Aluminum Garnet powder by the co-precipitation method, Material Science
and Engineering 288: 1–4..
Weiss, P. (1907a). Handbook of Modern Ferromagnetic Materials. Dordrecht, Netherlands: Kluwer Academic
Weiss, P. (1907b). Handbook of Modern Ferromagnetic Materials. Dordrecht,
Netherlands: Kluwer Academic
Widatallah, H. M., Johnson, C., Al-Harthi, S. H., Gismelseed, A. M., Al-Rawas, A.
D., Stewart, S. J., Elzain, M. E., Al-Omari, I. A. & Yousif, A. A. (2008). A
structural and mössbauer study of Y3Fe5O12 nanoparticles prepared with high
energy ball milling and subsequent sintering. Hyperfine Interactions, 183,
87–92.
Winkler, G. (1981). Magnetic Garnets. Hamburg, Germany: Friedr. Vieweg &
Sohn.
Wohlfarth, E. P. (Ed.).(1997). Ferromagnetic Garnets. Amsterdam, NY: North-Holland.
World Steel Association. (2014). World Steel in Figures 2014. Retrieved from
http://www.worldsteel.org/en/dam/World+Steel+in+Figures+2014+Final.pdf
.
© COPYRIG
HT UPM
103
Yamashita, T., & Hayes, P. (2008). Analysis of XPS Spectra of Fe2+ and Fe3+ ions
in oxide materials. Applied Surface Science, 254, 2441–2449.
Yu, H., Zeng, L., Lu, C., Zhang, W., & Xu, G. (2011). Synthesis of nanocrystalline
Yttrium Iron Garnet by low temperature solid state reaction. Materials
Characterization, 62, 378–381.
Zhao, H., Zhou, J., Bai, Y., Gui, Z., & Li, L. (2004). Effect of Bi-substitution on
the dielectric properties of polycrystalline Yttrium Iron Garnet. Journal of
Magnetism and Magnetic Materials, 280, 208–213.