**2.1 Ferromagnetism in Mn-doped SnO2**

Mn-doped SnO2 is an excellent candidate and promising materials for RTFM study, but only very little work has been reported so far compared to others. Among other preparation methods sol-gel preparation technique is best method for preparation of TM doped SnO2 thin film and nano structures [44, 45].

#### *2.1.1 Experimental*

*Magnetic Materials and Magnetic Levitation*

**Figure 1.**

less power of electricity, fast data processing speed, their memories are non-volatile [4]. Starting from metal-based technology, the research area of Spintronics shifted to the recent development of diluted magnetic semiconductors (DMS) materials which are compatible with standard semiconductor based electronics device**.** DMS are materials prepared through which a certain amount of the cations in a host semiconductor are partially replaced by transition metal ions (Mn, Ni, Co, Fe, Cr) as shown in **Figure 1** [5] as a result the materials attains both semiconducting and magnetic property which is makes these materials advantageous and applicable for Spintronics application. The total ferromagnetic behavior of these materials is linked to the interaction of the spin of the magnetic ions with the itinerant carriers [6–8]. DMS are important materials in the sense that logic, communications and storage operation can be achieved within the same materials technology [9, 10]. The property of achieving RTFM is one of the most important factors that determined DMS material to be used for practical spintronics application [7], The sp-d exchange mechanism between the d states of the TM doping and sp free carriers as well as the double exchange mechanisms are the main factor in the production of ferromagnetism in ODMS materials between d states of TM ions [11]. Among DMS materials oxide based DMS materials such as TM doped with HfO2, TiO2, ZnO and SnO2 are more advantageous than normal DMS materials and have important magnetic properties arises from a large sp-d exchange interactions between the magnetic ion elements and band electrons [9, 10, 12, 13]. ODMS has important special properties such as having high n-type carrier concentrations wide band gap, light transparency, capability to be grown at low temperatures, ecological safety and cheap [14–16]**.** Due to its n-type semiconductor, good conductivity, high carrier density and high chemical stability, SnO2 doped with TM is particularly promising materials for spintronic applications [17, 18]**.** SnO2 naturally existing in cassiterite form and it has tetragonal rutile structure and its wide band gap is about 3.6 eV [19, 20]. SnO2 has many technological applications, including gas sensors, solar cells, heat reflectors,

*Schematic view of a non-magnetic (left) semiconductor and a diluted magnetic semiconductor (right) [5].*

lithium ion batteries and other optoelectronic devices [21–23].

In the recent years the research field of RTFM in O-DMS has got more attention and many kinds of compounds have been discovered [24]. However, the idea behind the original source of ferromagnetism in these materials is not well understood a not complete it becomes the most challenging area in solid state physics [25]. Several groups have stated that the mechanism behind ferromagnetism in most O-DMS materials is the material's intrinsic property itself or the direct and indirect

**2. Ferromagnetism in oxide-based DMS**

**134**

SnMnO2 thin film is prepared by sol-gel method according to the literature reported [44]. The solution was prepared by dissolving a certain amount of tin tetrachloride SnCl4 and manganese nitrate hydrate [Mn (NO3)26H2O] in distilled water and

**Figure 2.** *M-H curves of (Ni-Mn) co-doped with SnO2 [11].*

ethanol respectively and stirring for 5 hour and aging for at least a week, the prepared solution was spin-coated on silicon substrate and heated at 120°C for 25 min. The film precursors were obtained after multilayer coating. Finally, to obtain SnMnO2 thin films, the precursors of films were calcinated in atmospheric air at 5000°C for an hour.

As reported by Tian et al., the chemical co-precipitation method was used to synthesize Mn doped SnO2 nanoparticles [46]. First, appropriate quantities of SnCl2 and manganese acetic acid were dissolved in ethanol solution, then a few drops of HCl solution were applied to ensure dissolution. Then a 10 M ammonium bicarbonate solution with continuous stirring at 60°C was applied to the mixture solution until a pH of 9 was reached. After being distributed by ultrasonic for 15 min to get nano-crystalline powders. The resulting precipitation washed to clean the impurities and dried in air at 150°C. Finally, the nano crystalline powders were sintered in the air for 3 hours. X-ray diffraction (XRD) recorded the crystal structure of the synthesized SnMnO2 thin film as shown in **Figures 3** and **4**. The study magnetization property and RTFM were performed using a superconductive quantum interference device (SQUID) and vibrating sample magnetometer (VSM) respectively.

### *2.1.2 Result and discussion*

According to various reports, the origin of the observed FM in Mn-doped SnO2 depends on a number of factors; some reported that Mn- SnO2 prepared by PLD method exhibits the only paramagnetic behavior [47]. Similarly, others reported that the dopant Mn does not contribute any role for the observed FM behavior of Mn-doped SnO2 films; it is assumed that oxygen vacancies and defects are the main factors contributing to the FM order in the system as shown in **Figure 5** below [48]. Others report on Mn-SnO2 powders confirmed that the observed FM property is likely the results from oxygen vacancies, and Mn doping has only a significant role of the observed source of RTFM in the materials [49]. High level of Mn dopant can degrade the FM behavior where as small doping concentration intrinsic defects can act as a source of the FM in Mn-doped SnO2 due to a very large magnetic moment [39]. On the other hand, a study reported on Mn doped SnO2 nanoparticles shows sintering temperature and doping concentration can affects the magnetism of the materials system [46]. As shown in **Figure 7** that Mn-doped SnO2 powder that concentration of Mn ion contributes to a decrease in the average magnetic moment of magnetic ions, this is due to the competition between the super-exchange antiferromagnetic coupling and the F-center coupling mechanism [50]**.** Similarly, other research on Mn-doped SnO2 thin films

**137**

*2.2.1 Experimental*

**Figure 4.**

**Figure 5.**

**2.2 Ferromagnetism in Fe-doped SnO2**

*Ferromagnetism in SnO2 Doped with Transition Metals (Fe, Mn and Ni) for Spintronics…*

synthesized by sol-gel method show that dopants and electronic cloud interactions play a significant role in establishing FM [44]**.** The ferromagnetic property of Mn doped SnO2 confirmed that BMP's overlapping, oxygen vacancies and F-center exchange interaction are the cause for the existence of ferromagnetic behavior in in pure and doped Mn doped SnO2 materials [51]**.** The increment of Mn concentration lead to the decline of magnetic moment of the origin of ferromagnetism behavior in Mn-doped SnO2 films is explained BMP and the average magnetic moment per Mn concentration decreases with increasing Mn content [44]. Overall, the origin of FM in Mn doped SnO2 system is still controversial and there is no such exact cause FM in this material.

*RTFM for undoped and Mn doped tin oxide thin films, room temperature ferromagnetism.*

Rodrı et al. reported that Fe-SnO2 thin films on the LaAlO3 subtract were synthesized with PLD techniques. The doped SnO2 target was synthesized with metallic Fe powders and SnO2. The powders were mixed with a ball-mill for 2 minutes,

*DOI: http://dx.doi.org/10.5772/intechopen.90902*

*XRD patterns of SnMnO2 nano particle [46].*

**Figure 3.** *XRD patterns of SnMnO2 films [44].*

*Ferromagnetism in SnO2 Doped with Transition Metals (Fe, Mn and Ni) for Spintronics… DOI: http://dx.doi.org/10.5772/intechopen.90902*

**Figure 4.**

*Magnetic Materials and Magnetic Levitation*

*2.1.2 Result and discussion*

ethanol respectively and stirring for 5 hour and aging for at least a week, the prepared solution was spin-coated on silicon substrate and heated at 120°C for 25 min. The film precursors were obtained after multilayer coating. Finally, to obtain SnMnO2 thin films, the precursors of films were calcinated in atmospheric air at 5000°C for an hour. As reported by Tian et al., the chemical co-precipitation method was used to synthesize Mn doped SnO2 nanoparticles [46]. First, appropriate quantities of SnCl2 and manganese acetic acid were dissolved in ethanol solution, then a few drops of HCl solution were applied to ensure dissolution. Then a 10 M ammonium bicarbonate solution with continuous stirring at 60°C was applied to the mixture solution until a pH of 9 was reached. After being distributed by ultrasonic for 15 min to get nano-crystalline powders. The resulting precipitation washed to clean the impurities and dried in air at 150°C. Finally, the nano crystalline powders were sintered in the air for 3 hours. X-ray diffraction (XRD) recorded the crystal structure of the synthesized SnMnO2 thin film as shown in **Figures 3** and **4**. The study magnetization property and RTFM were performed using a superconductive quantum interference device (SQUID) and vibrating sample magnetometer (VSM) respectively.

According to various reports, the origin of the observed FM in Mn-doped SnO2 depends on a number of factors; some reported that Mn- SnO2 prepared by PLD method exhibits the only paramagnetic behavior [47]. Similarly, others reported that the dopant Mn does not contribute any role for the observed FM behavior of Mn-doped SnO2 films; it is assumed that oxygen vacancies and defects are the main factors contributing to the FM order in the system as shown in **Figure 5** below [48]. Others report on Mn-SnO2 powders confirmed that the observed FM property is likely the results from oxygen vacancies, and Mn doping has only a significant role of the observed source of RTFM in the materials [49]. High level of Mn dopant can degrade the FM behavior where as small doping concentration intrinsic defects can act as a source of the FM in Mn-doped SnO2 due to a very large magnetic moment [39]. On the other hand, a study reported on Mn doped SnO2 nanoparticles shows sintering temperature and doping concentration can affects the magnetism of the materials system [46]. As shown in **Figure 7** that Mn-doped SnO2 powder that concentration of Mn ion contributes to a decrease in the average magnetic moment of magnetic ions, this is due to the competition between the super-exchange antiferromagnetic coupling and the F-center coupling mechanism [50]**.** Similarly, other research on Mn-doped SnO2 thin films

**136**

**Figure 3.**

*XRD patterns of SnMnO2 films [44].*

*XRD patterns of SnMnO2 nano particle [46].*

**Figure 5.** *RTFM for undoped and Mn doped tin oxide thin films, room temperature ferromagnetism.*

synthesized by sol-gel method show that dopants and electronic cloud interactions play a significant role in establishing FM [44]**.** The ferromagnetic property of Mn doped SnO2 confirmed that BMP's overlapping, oxygen vacancies and F-center exchange interaction are the cause for the existence of ferromagnetic behavior in in pure and doped Mn doped SnO2 materials [51]**.** The increment of Mn concentration lead to the decline of magnetic moment of the origin of ferromagnetism behavior in Mn-doped SnO2 films is explained BMP and the average magnetic moment per Mn concentration decreases with increasing Mn content [44]. Overall, the origin of FM in Mn doped SnO2 system is still controversial and there is no such exact cause FM in this material.

#### **2.2 Ferromagnetism in Fe-doped SnO2**

#### *2.2.1 Experimental*

Rodrı et al. reported that Fe-SnO2 thin films on the LaAlO3 subtract were synthesized with PLD techniques. The doped SnO2 target was synthesized with metallic Fe powders and SnO2. The powders were mixed with a ball-mill for 2 minutes,

then pressed uniaxially (200 MPa) into a disk and finally sintered at 1000°C [52]. The crystallographic structures of the prepared Fe doped SnO2 were determined by X-ray diffraction (XRD) and the magnetic measurements were performed with superconducting quantum interference device (SQUID).

### *2.2.2 Result and discussion*

There have been reports of Fe doped SnO2 in which the ferromagnetic interactions between magnetic impurities mediated oxygen or free carriers in the Fe doped SnO2 system responsible for forming FM. Similarly, defects in undoped SnO2 semiconductors may contribute to the observed ferromagnetism [33, 53]. Similarly both undoped and Fe-doped SnO2 thin films shows the observed FM property is due to oxygen vacancies near Fe increased the magnetic moment, the RTFM behavior observed in the SnO2 film must be associated with the sample shape or to defects incorporated during film growth and, part of the magnetism observed in SnO2 as shown in figure [52]. The results from Fe-doped SnO2 powders prepared by polymerized complex method confirms that the annealing temperature contributes to decline of magnetic saturation which is related to the defects rather than from dopant iron sites shown in **Figure 6a** below [54, 55] the existence of vacancies and defects in the grain boundaries and interfaces in Fe doped SnO2 nanoparticles leads to decline the ferromagnetic behavior of system [56]. The decrease in Fe ion's magnetic moments, with their doping concentrations increasing, The superexchange interaction may result in the interaction between neighboring TM-ions of the anti-ferromagnetic form, resulting in the observed decrease in the magnetic moment with increased concentration of TM as shown in **Figure 10** [57]. The work of the other group reporting shows that the lattice distortion induced by co-doping Fe-SnO2 enhance ferromagnetic saturation magnetization of the compared with not co-doped one [26]**.** As shown in **Figure 7** oxygen vacancies has a great impact on the FM property of Fe doped SnO2 [58]. The ferromagnetic behavior of Fe-doped SnO2 thin films is caused by the coupling of ferric ions through an electron trapped in an oxygen vacancy [59]**.** In some cases the introduction of iron in semiconducting nano particles SnO2 is responsible for appearance of paramagnetic behavior of the system that is due to weak antiferromagnetic interaction [60]. The decline of antiferromagnetic interaction in Fe-SnO2 nano particles was reduced by the increment of Fe concentration [61]. Some study reported that the magnetic properties Fe-doped SnO2 nano powders shows that the an increased Fe concentration leading to the reduction of oxygen-related vacancy changes magnetic property to paramagnetic

**139**

**Figure 8.**

**Figure 7.**

*2.3.1 Experimental*

temperatures and low temperatures.

**2.3 Ferromagnetism in Ni doped SnO2**

*Ferromagnetism in SnO2 Doped with Transition Metals (Fe, Mn and Ni) for Spintronics…*

*Sn1−x FexO2 film hysteresis loops with different concentration at 300 K. The inset is the difference in the* 

system as shown in **Figure 8** and the FM interactions is based on Bound Magnetic Polarons (BMPs) formation [62]. Sometimes the host systems SnO2 and SnO doped with Fe during sample preparation can affect the observed magnetic properties of the system [63]. Another study confirms that changes in temperature play a role in the magnetic transition from paramagnetic to ferromagnetic behavior at ambient

*RT magnetization versus magnetic field curves for the Fe-doped SnO2 nano powders [62].*

As reported in the literature SnNiO2 films were prepared by sol-gel method [64]

the same procedure as [44]. The solution was prepared by dissolving SnCl4 and

*DOI: http://dx.doi.org/10.5772/intechopen.90902*

*concentration of Fe doping in saturation magnetization [58].*

**Figure 6.** *Fe doped SnO2 magnetic hysteresis annealed for certain hours at different temperatures [54].*

*Ferromagnetism in SnO2 Doped with Transition Metals (Fe, Mn and Ni) for Spintronics… DOI: http://dx.doi.org/10.5772/intechopen.90902*

#### **Figure 7.**

*Magnetic Materials and Magnetic Levitation*

*2.2.2 Result and discussion*

superconducting quantum interference device (SQUID).

then pressed uniaxially (200 MPa) into a disk and finally sintered at 1000°C [52]. The crystallographic structures of the prepared Fe doped SnO2 were determined by X-ray diffraction (XRD) and the magnetic measurements were performed with

There have been reports of Fe doped SnO2 in which the ferromagnetic interactions between magnetic impurities mediated oxygen or free carriers in the Fe doped SnO2 system responsible for forming FM. Similarly, defects in undoped SnO2 semiconductors may contribute to the observed ferromagnetism [33, 53]. Similarly both undoped and Fe-doped SnO2 thin films shows the observed FM property is due to oxygen vacancies near Fe increased the magnetic moment, the RTFM behavior observed in the SnO2 film must be associated with the sample shape or to defects incorporated during film growth and, part of the magnetism observed in SnO2 as shown in figure [52]. The results from Fe-doped SnO2 powders prepared by polymerized complex method confirms that the annealing temperature contributes to decline of magnetic saturation which is related to the defects rather than from dopant iron sites shown in **Figure 6a** below [54, 55] the existence of vacancies and defects in the grain boundaries and interfaces in Fe doped SnO2 nanoparticles leads to decline the ferromagnetic behavior of system [56]. The decrease in Fe ion's magnetic moments, with their doping concentrations increasing, The superexchange interaction may result in the interaction between neighboring TM-ions of the anti-ferromagnetic form, resulting in the observed decrease in the magnetic moment with increased concentration of TM as shown in **Figure 10** [57]. The work of the other group reporting shows that the lattice distortion induced by co-doping Fe-SnO2 enhance ferromagnetic saturation magnetization of the compared with not co-doped one [26]**.** As shown in **Figure 7** oxygen vacancies has a great impact on the FM property of Fe doped SnO2 [58]. The ferromagnetic behavior of Fe-doped SnO2 thin films is caused by the coupling of ferric ions through an electron trapped in an oxygen vacancy [59]**.** In some cases the introduction of iron in semiconducting nano particles SnO2 is responsible for appearance of paramagnetic behavior of the system that is due to weak antiferromagnetic interaction [60]. The decline of antiferromagnetic interaction in Fe-SnO2 nano particles was reduced by the increment of Fe concentration [61]. Some study reported that the magnetic properties Fe-doped SnO2 nano powders shows that the an increased Fe concentration leading to the reduction of oxygen-related vacancy changes magnetic property to paramagnetic

**138**

**Figure 6.**

*Fe doped SnO2 magnetic hysteresis annealed for certain hours at different temperatures [54].*

*Sn1−x FexO2 film hysteresis loops with different concentration at 300 K. The inset is the difference in the concentration of Fe doping in saturation magnetization [58].*

**Figure 8.** *RT magnetization versus magnetic field curves for the Fe-doped SnO2 nano powders [62].*

system as shown in **Figure 8** and the FM interactions is based on Bound Magnetic Polarons (BMPs) formation [62]. Sometimes the host systems SnO2 and SnO doped with Fe during sample preparation can affect the observed magnetic properties of the system [63]. Another study confirms that changes in temperature play a role in the magnetic transition from paramagnetic to ferromagnetic behavior at ambient temperatures and low temperatures.

#### **2.3 Ferromagnetism in Ni doped SnO2**

#### *2.3.1 Experimental*

As reported in the literature SnNiO2 films were prepared by sol-gel method [64] the same procedure as [44]. The solution was prepared by dissolving SnCl4 and

NiCl2·6H2O in distilled water and ethanol. For the film preparation, to get the thin films the solution was spin-coated on silicon substrate. As reported by [57] undoped and Ni doped SnO2 prepared using a method of co-precipitation, the solution was prepared by dissolving SnCl4.5H2O and NiCl2.5H2O properly into de-ionized water. After the white precipitates were obtained, ammonium hydroxide (NH4OH) was added with stirring to the solution. The resulting mixtures were washed with de-ionized water to remove unwanted ionic impurities that may develop during the process of synthesis. Such washed precipitates were dried in air and Ni doped SnO2 powder products were eventually obtained.

Detail crystallographic structures of the prepared SnNiO2 thin films and powders were carried out using XRD and the details of the magnetic properties were probed by vibrating sample magnetometer (VSM) measurements.

### *2.3.2 Result and discussion*

According to recent experimental investigation of RTFM on Ni doped SnO2 has made it important and promising materials for spintronics application [64–68]. The observed FM in these materials is linked to oxygen vacancy and structural defects of the materials [67]. In some cases, nano-crystalline Ni doped SnO2 exhibits Paramagnetic character [68]. As shown in **Figure 9** the super-exchange interaction may result in an anti-ferromagnetic type interaction between neighboring TM-ions, resulting in a decline in magnetic moment with an increase in TM concentration [57]**.** In some studies the introduction of more Ni doping concentration leads for reduction of magnetic moment Ni ion of because the antiferromagnetic superexchange interaction among closest neighbor in Ni2+ ions in Ni doped SnO2 samples the BMP model can explain for RTFM on these systems on the other hand nickel (Ni) doped SnO2 powder shows a substitution of Sn atom by Ni atom interstitially lead to the appearance of diamagnetic state [64]. Kuppan et al. shows that oxygen vacancy around magnetic impurity plays a major role in establishing ferromagnetism in Ni doped SnO2. Nevertheless, saturation magnetization slowly decreases with a persistent rise in Ni doping concentration [68]. Thus we strongly feels that

**141**

**3. Conclusion**

**Figure 10.**

*Ferromagnetism in SnO2 Doped with Transition Metals (Fe, Mn and Ni) for Spintronics…*

the oxygen vacancy and or defects in the Ni doped SnO2 system. Similarly a report from Ni-doped SnO2 nanoparticles synthesized by a polymer precursor method demonstrated that doping small amount of Ni doping concentration can push defect-related FM while introducing high Ni concentration favors the paramagnetic phase stabilization [70]. Similarly oxygen vacancy and defects on Ni doped SnO2 thin film contribute for the formation RTFM [71]. As shown in **Figure 10** some studies have confirmed that Ni ions doping creates numerous defects or oxygen vacancies in SnO2 nanoparticles in order to introduce RTFM in SnO2 nanoparticles [69]. Some reported that substrates on thin film deposition have a strong impact on the magnetic moment of these material and the result confirmed that that FM in the films is as result of the doped matrix grown in different substrates [65]. In some cases the decrease of magnetic moment of per Ni ion is observed with the introduction of more dopants Ni ions that is associated with antiferromagnetic superexchange interaction between in Ni ions in the system [64, 72]. Some reported that the mechanism of the observed FM in nickel (Ni) doped tin oxide thin films can be

Most of the results reported in the review shows that the perfect mechanism of induced FM in Mn, Fe and Ni doped SnO2 is related to the intrinsic nature of the material itself, especially oxygen vacancies and defects of the crystal formed during sample preparation and doping magnetic impurity influence the magnetism of the systems. Even though, a different type of FM is reported. However, the different reported results are contradictory with each other and further research is needed to

explained in bound magnetic polaron (BMP) mode [73].

*Room temperature magnetization for pure and Ni doped SnO2 NPs [69].*

bring new solution for the contradiction idea behind FM.

*DOI: http://dx.doi.org/10.5772/intechopen.90902*

**Figure 9.** *The RTFM hysteresis of SnFeO2 and SnNiO2 at different doping concentration [57].*

*Ferromagnetism in SnO2 Doped with Transition Metals (Fe, Mn and Ni) for Spintronics… DOI: http://dx.doi.org/10.5772/intechopen.90902*

#### **Figure 10.**

*Magnetic Materials and Magnetic Levitation*

powder products were eventually obtained.

*2.3.2 Result and discussion*

NiCl2·6H2O in distilled water and ethanol. For the film preparation, to get the thin films the solution was spin-coated on silicon substrate. As reported by [57] undoped and Ni doped SnO2 prepared using a method of co-precipitation, the solution was prepared by dissolving SnCl4.5H2O and NiCl2.5H2O properly into de-ionized water. After the white precipitates were obtained, ammonium hydroxide (NH4OH) was added with stirring to the solution. The resulting mixtures were washed with de-ionized water to remove unwanted ionic impurities that may develop during the process of synthesis. Such washed precipitates were dried in air and Ni doped SnO2

Detail crystallographic structures of the prepared SnNiO2 thin films and powders were carried out using XRD and the details of the magnetic properties were

According to recent experimental investigation of RTFM on Ni doped SnO2 has made it important and promising materials for spintronics application [64–68]. The observed FM in these materials is linked to oxygen vacancy and structural defects of the materials [67]. In some cases, nano-crystalline Ni doped SnO2 exhibits Paramagnetic character [68]. As shown in **Figure 9** the super-exchange interaction may result in an anti-ferromagnetic type interaction between neighboring TM-ions, resulting in a decline in magnetic moment with an increase in TM concentration [57]**.** In some studies the introduction of more Ni doping concentration leads for reduction of magnetic moment Ni ion of because the antiferromagnetic superexchange interaction among closest neighbor in Ni2+ ions in Ni doped SnO2 samples the BMP model can explain for RTFM on these systems on the other hand nickel (Ni) doped SnO2 powder shows a substitution of Sn atom by Ni atom interstitially lead to the appearance of diamagnetic state [64]. Kuppan et al. shows that oxygen vacancy around magnetic impurity plays a major role in establishing ferromagnetism in Ni doped SnO2. Nevertheless, saturation magnetization slowly decreases with a persistent rise in Ni doping concentration [68]. Thus we strongly feels that

probed by vibrating sample magnetometer (VSM) measurements.

*The RTFM hysteresis of SnFeO2 and SnNiO2 at different doping concentration [57].*

**140**

**Figure 9.**

*Room temperature magnetization for pure and Ni doped SnO2 NPs [69].*

the oxygen vacancy and or defects in the Ni doped SnO2 system. Similarly a report from Ni-doped SnO2 nanoparticles synthesized by a polymer precursor method demonstrated that doping small amount of Ni doping concentration can push defect-related FM while introducing high Ni concentration favors the paramagnetic phase stabilization [70]. Similarly oxygen vacancy and defects on Ni doped SnO2 thin film contribute for the formation RTFM [71]. As shown in **Figure 10** some studies have confirmed that Ni ions doping creates numerous defects or oxygen vacancies in SnO2 nanoparticles in order to introduce RTFM in SnO2 nanoparticles [69]. Some reported that substrates on thin film deposition have a strong impact on the magnetic moment of these material and the result confirmed that that FM in the films is as result of the doped matrix grown in different substrates [65]. In some cases the decrease of magnetic moment of per Ni ion is observed with the introduction of more dopants Ni ions that is associated with antiferromagnetic superexchange interaction between in Ni ions in the system [64, 72]. Some reported that the mechanism of the observed FM in nickel (Ni) doped tin oxide thin films can be explained in bound magnetic polaron (BMP) mode [73].

### **3. Conclusion**

Most of the results reported in the review shows that the perfect mechanism of induced FM in Mn, Fe and Ni doped SnO2 is related to the intrinsic nature of the material itself, especially oxygen vacancies and defects of the crystal formed during sample preparation and doping magnetic impurity influence the magnetism of the systems. Even though, a different type of FM is reported. However, the different reported results are contradictory with each other and further research is needed to bring new solution for the contradiction idea behind FM.

*Magnetic Materials and Magnetic Levitation*
