Mn2O3納米結(jié)構(gòu)的簡(jiǎn)易合成與電化學(xué)性質(zhì)

趙 丹 譚金山 季倩倩 張進(jìn)濤 趙修松, 郭培志＊,

(1青島大學(xué)纖維新材料與現(xiàn)代紡織國(guó)家重點(diǎn)實(shí)驗(yàn)室培育基地多功能材料研究所，青島 266071)

(2青島大學(xué)化學(xué)化工與環(huán)境學(xué)院，青島 266071)(3Department of Chemical and Biomolecular Engineering,National University of Singapore,4 Engineering Drive 4,Singapore 117576)

Mn2O3納米結(jié)構(gòu)的簡(jiǎn)易合成與電化學(xué)性質(zhì)

趙 丹1,2譚金山1季倩倩1,2張進(jìn)濤3趙修松1,2,3郭培志＊,1,2

(1青島大學(xué)纖維新材料與現(xiàn)代紡織國(guó)家重點(diǎn)實(shí)驗(yàn)室培育基地多功能材料研究所，青島 266071)

(2青島大學(xué)化學(xué)化工與環(huán)境學(xué)院，青島 266071)(3Department of Chemical and Biomolecular Engineering,National University of Singapore,4 Engineering Drive 4,Singapore 117576)

用簡(jiǎn)易的室溫或水熱方法制備出不同形貌的MnCO3微結(jié)構(gòu)。經(jīng)600℃熱處理后，室溫制備MnCO3轉(zhuǎn)變成Mn2O3膠體片，而水熱制備MnCO3樣品則形成多孔Mn2O3納米結(jié)構(gòu)。然而，室溫制備MnCO3經(jīng)120℃熱處理后形成Mn2O3晶相。制備樣品經(jīng)過XRD和SEM表征表明，熱處理MnCO3前驅(qū)物形成Mn2O3過程導(dǎo)致產(chǎn)物形貌與結(jié)構(gòu)變化。其形成機(jī)理又通過TEM和FTIR進(jìn)一步研究。Mn2O3納米結(jié)構(gòu)的電容性質(zhì)通過循環(huán)伏安法表征，結(jié)果表明Mn2O3形貌與結(jié)構(gòu)對(duì)其電容有重要影響。

Mn2O3；MnCO3；水熱合成；電容

Nanostructured materials for energy storage and conversation have been received more and more attention due to their potential applications in the fields of portable electronic devices and hybrid electric vehicles(HEVs)[1-3].Supercapacitors become promising energy storage devices because of its high power density,high cycle efficiency,and long cycle life[4-5].Precious metal oxides can show ideal pseudocapacitive behaviors,however,the high cost limits their practical applications[6-7].Over the past decades,manganese oxides(MnOx)have been explored due to its low cost,variable oxidation states,excellent capacitance and cycle performances[8-12].Various manganese oxides with controlled morphologies and structures have been successfully synthesized using different approaches including hydrothermal method[13-15],sol-gel process[16-19],electrochemical route[20-21],template synthesis[22],and solution-chemical synthesis[23-25].For example,MnO2film electrode showed a capacitance as high as 1 380 F·g-1,in which MnO2spherical grains were fabricated by a coprecipitation method using KMnO4and MnSO4as the reagents[12].Mn2O3nanoparticles can be formedviahydrothermalprocessesofaqueousKMnO4solutions with the addition of different alcohols[25],while Mn2O3nanowires with excellent electrocatalytic properties for the reduction of O2can be synthesized controllably based on the systems containing Mn(NO3)2and sodium dodecylbenzenesulfonate(SDBS)[15].Our recent results show that organized mesoporous carbon decorated with Mn2O3nanoparticles can be used as the electrode materialsforsupercapacitorand Mn2O3nanoparticles display high specific capacitances as calculated from the content of Mn2O3phase in the electrode and the increase in capacitance of the composite electrode[26].However,the relationship between the structures and capacitances of Mn2O3nanomaterials still need to be further clarified.

In this paper,the morphology-controlled synthesis of Mn2O3nanostructures as well as their effect on the capacitance isstudied.Itisfound thatMnCO3aggregates or Mn2O3nanostructures can be obtained based on the systems containing biomolecule L-cysteine and KMnO4.These results are different from our earlier results that hexagonal γ-MnS nanorod crystals can be controllably fabricated after the hydrothermal processes of the mixed solutions containing manganesesalts and L-cysteine[27].The present experimental results reveal that hexagonal Mn2O3nanoplates can be obtained after high-temperature treatments of the roomtemperature products(Mn-RT)prepared from the reaction of KMnO4and L-cysteine.However,porous Mn2O3nanostructures are formed after heat treatments of MnCO3precursors synthesized by hydrothermal treatments of Mn-RT samples.The electrochemical properties of these Mn2O3nanostructures are studied by cyclic voltammetry.

1 Experimental

1.1 Materials

Alcohols,KMnO4,Na2SO4and L-cysteine were of analytical grade(Sinopharm Chemical Reagent Company)and used without further purification.Acetylene carbon black(99.99%)and polytetrafluorothylene latex(PTFE,60%)were purchased form Strem Chemicals and Sigma-Aldrich,respectively.

1.2 Synthesis of Mn2O3nanoplates and porous nanostructures

In a typical synthesis,aqueous KMnO4(0.474 g)solution(15 mL)was dropped into aqueous L-cysteine(0.363 g)solution(15 mL)under stirring.After 5 min stirring,the solution was transferred to a 40 mL teflonlined autoclave.Hydrothermal synthesis was carried out in an oven at 120 or 150℃for 24 h.The solid was collected and washed with distilled water and absolute ethanol thoroughly,and then dried in an oven at 60℃for 6 h.The products obtained at room temperature,120 and 150℃are abbreviated as Mn-RT,MnCO3-120 and MnCO3-150,respectively.These three products were further calcined in a tube furnace at 600℃in air for 3 h to obtain the as-prepared products Mn2O3-RT,Mn2O3-120 and Mn2O3-150,respectively.Furthermore,Mn2O3-RT-L sample is referred to the product of Mn-RT sample after heat treatment at 120℃in air for 3 h.

1.3 Characterization

XRD patterns were recorded on a Bruker D8 Advance X-ray diffractometer equipped with graphite monochromatized Cu Kα radiation(λ =0.154 18 nm)from 10°to 80°(2θ)using a solid detector.SEM images were taken with a JSM-6390LV scanning electron microscope operated at 20 kV.TEM images were obtained with a JEM-2000EX transmission electron microscope operated at 160 kV.FTIR spectra were measured on a Nicolet5700 FTIR spectrometer.Electrochemical measurements were performed on a CHI760C electrochemical workstation using a threeelectrode cell,platinum wire as the counter electrode and saturated calomel electrode as the reference electrode in 1 mol·L-1Na2SO4solution,the working electrode was prepared by mixing the Mn2O3samples with polytetrafluoroethylene(PTFE)and acetylene carbon black in a mass ratio of 80:15:5 and was blended to achieve a homogeneous mixture.The resulting slurry was then pressed onto a nickel foam grid(1×1 cm2)at 15 MPa.The typical mass load of each electrode material is about 5 mg.Before measurements,the working electrodes are dipped into aqueous 1 mol·L-1Na2SO4solutions overnight.All potentials are reported against the saturated calomel reference electrode.

2 Results and discussion

Fig.1 shows the XRD patterns of as-prepared samples.It can be seen from Fig.1a that no crystalline phase is formed in Mn-RT sample,indicating an amorphous structure.After a hydrothermal process at 120 ℃,the XRD pattern of MnCO3-120 in Fig.1b can be indexed to rhodochrosite MnCO3phase(PDF No.86-0172).When the synthesis temperature is up to 150 ℃,the diffraction peaks in Fig.1c of sample MnCO3-150 can also be well-indexed to the same MnCO3phase,and the peak at 34.4°ascribed to the(006)peak is strongly strengthened.Furthermore,the narrow and intensive diffraction peaks in Fig.1c indicate that the MnCO3-150 products are well crystallized.

Fig.1 XRD patterns of the as-prepared products

The SEM images of these products are shown in Fig.2.Mn-RT(Fig.2a)shows clew-like microstructures composed of nanoparticles and some crossed wire-like structures with several micrometers long and diameter scales of tens of nanometers.It can be seen from Fig.2b that sample MnCO3-120 displays spindle-like shape with length scale about 1.5～2 μm composed of MnCO3nanoparticles.However,MnCO3-150 showed larger micro-aggregate structure composed of MnCO3nanoparticles compared to those of MnCO3-120(in Fig.2c).It can be observed that the reaction temperature has a strong effect on the morphology of the MnCO3products.The formation of MnCO3micro-aggregates composed of MnCO3particles could be ascribed to the Ostwald ripening that large particles grow at the expense of smaller ones[28-29].This has been further confirmed by the results ofthe intermediate products synthesized hydrothermally at different reaction times.It can be observed from Fig.3a and d that both the products obtained after 2 h reaction at 120 and 150℃,respectively,display similar morphology to that of Mn-RT(in Fig.2a).With the reaction time extended to 4 h,however,the morphology changes dramatically(Fig.3b and e).When the reaction time is 8 h,spindle-like aggregates with the size less than 1 m can be observed for the products collected at 120℃while somewhat larger particles and aggregates are formed when the synthesis temperature is up to 150 ℃ (Fig.3c and f).

Fig.2 SEM images of Mn-RT(a),MnCO3-120(b)and MnCO3-150(c)

The XRD patterns of the products obtained by different heat treatments are shown in Fig.4.It can be seen from Fig.4a～c that the diffraction peaks in the XRD patterns of sample Mn2O3-RT,Mn2O3-120 and Mn2O3-150,respectively,can be well indexed to the same bixbyite Mn2O3phase(PDF No.41-1442).These results indicate that both amorphous Mn-RT sample and crystalline MnCO3products can be transited to Mn2O3phases after the heat treatment at 600 ℃ in air.Interestingly,it is Mn2O3phase,not MnCO3phase or MnO2phase,that can also be obtained for the Mn2O3-RT-L sample as evidenced by the XRD pattern in Fig.4d.This is clearly different from that of sample MnCO3-120 synthesized using sample Mn-RT as the raw material via a hydrothermal process at 120℃.Furthermore,the total weight loss for the formation of Mn2O3sample from MnCO3precursor under high temperature treatments is 31%,in good agreement with the theoretical value calculated from the following reaction:

Fig.4 XRD patterns of the calcined samples

Fig.3 SEM images of the intermediate products synthesized from the mixed systems at 120 ℃(a,b,c)and 150℃(d,e,f)for 2 h(a,d),4 h(b,e)and 8 h(c,f)

Generally,Mn2O3phases are formed from Mncontaining compounds after high temperature treatments.Recently,it is reported that Mn2O3phases can be formed during the reaction of KMnO4with active mesoporous carbon materials[26]or specific alcohols[25]at room temperature.Our results show that Mn2O3phase,not MnCO3or MnO2phase,can be formed from Mn-RT samples after low temperature treatmentalthough impurities are also found in the sample according to the FTIR spectrum(Fig.5a).For example,the peaks at 2 922 and 2 850 cm-1ascribed to CH2symmetric and asymmetric vibrations,respectively,appear,indicating that the alkyl groups still exist in the Mn2O3-RT-L samples.Two peaks at 3 422 and 1 630 cm-1in Fig.5a can be observed,which are assigned to H2O absorbed by KBr.The FTIR spectra of the Mn2O3samples obtained after high temperature treatmentofthe precursors are obviously different from that of sample Mn-RT-L.From Fig.5b～d,it can be clearly seen that all the Mn2O3samples show similar absorption spectra only with some differences in absorption intensities of the characteristic peaks.For example,the peaks at 3 422 and 1630 cm-1can also be observed similar to those of sample Mn-ER-L.The peaks around 530,604,and 665 cm-1and the peaks between 1 000～1 200 cm-1assigned to νMn-Oof Mn2O3phase[30],indicating that pure Mn2O3phase can be formed after the high temperature process.

Fig.5 FTIR spectra of Mn2O3-RT-L(a),Mn2O3-RT(b),Mn2O3-120(c)and Mn2O3-150(d)

Compare to those results of the precursors shown in Fig.2,obvious change in the shape of products can be observed for the Mn2O3samples.Fig.6a shows the SEM image of sample Mn2O3-RT-L.The sample displays irregular shapes decreasing greatly in the size of the aggregates compared with those of Mn-RT samples.This may be caused by the collapse of Mn-RT samples under heat treatments.It is interesting to note that colloidal Mn2O3particles shown in Fig.6b display narrow size distribution with the size scales less than 150 nm.Spindle Mn2O3microstructures with the length scales of 1～2 μm composed of colloidal particles can be observed from sample Mn2O3-120(Fig.6c),in which the shape and the size of the aggregates are similar to those ofthe MnCO3-120 precursor.However,porous nanostructure aggregates can be obtained for sample Mn2O3-150(Fig.6d),in which the contour of Mn2O3aggregates is maintained compared with those of MnCO3-150 samples.It can also be observed clearly from Fig.6d that the sizes of Mn2O3-150 particles are smaller than those of Mn2O3-120 colloidal particles.

The TEM images of Mn2O3samples are shown in Fig.7.The TEM image(Fig.7a)of sample Mn2O3-RT displays plate-like nanostructures with clear edges and somewhat irregular～hexagonal shapes.The sizes of the Mn2O3-RT colloid plates are of 50～120 nm in accord with those of SEM observations(Fig.6B).The selected area electron diffraction(SAED)pattern of a single Mn2O3plate in the inset in Fig.7a shows that Mn2O3colloidal plates are single crystalline.The TEM image of sample Mn2O3-120(Fig.7b)reveals that the porous spindle microstructures are composed of irregular colloidal Mn2O3particles with the sizes similar to those of Mn2O3-RT.The SAED patterns of a single particle,as depicted in the inset in Fig.7b,shows that Mn2O3particles are single crystalline.Interestingly,sample Mn2O3-150 shows similar morphology with those of Mn2O3-120 and is composed of Mn2O3nanoparticles with the size of 30～60 nm(Fig.7c).The SAED pattern in the inset in Fig.7c shows the single crystal nature of a single Mn2O3nanoparticle.

Fig.6 SEM images of Mn2O3-RT-L(a),Mn2O3-RT(b),Mn2O3-120(c)and Mn2O3-150(d)

Fig.7 TEM images of Mn2O3-RT(a),Mn2O3-120(b),and Mn2O3-150(c)

Cyclic voltammograms(CV)for Mn2O3samples at different scan rates are shown in Fig.8.The CV curves of the samples are rectangular profiles at low scan rates,indicating the existence of an ideal capacitive behavior important for a system to be highly reversible.The specific capacitance of Mn2O3-150 in Fig.8Ca is 93 F·g-1at the scan rate of 2 mV·s-1,which is the highest in the present study.For sample Mn2O3-120 and Mn2O3-RT,the specific capacitances are found to be 72 and 67 F·g-1(Fig.8Ba and Aa),respectively.If the scan rate is changed to 5 mV·s-1,the calculated specific capacitances for sample Mn2O3-150,Mn2O3-120 and Mn2O3-RT are 58,50 and 51 F·g-1,respectively.The CV curves are not nearly rectangular at a scan rate of 10 mV·s-1,as shown in the c curves in Fig.8,indicating that the ohmic resistance of the samples is large at a high scan rate[31].The main difference in the specific capacitance for these Mn2O3samples may be attributed to the difference in the size and structure nature of the synthesized materials.As pseudocapacitance is related to the actual redox reactions occurring in the system,the reactivity of the samples may be strengthed by large surface area small particles with a facile diffusion of electrolyte ions.It should be pointed that the specific capacitance values of the Mn2O3samples are smaller than those of MnO2samples[10,20].This may be caused by the existence of the 3+oxidation state of Mn leading to the reduction in the specific capacitance.

Fig.8 CV curves of sample Mn2O3-RT(A),Mn2O3-120(B)and(C)Mn2O3-150 in aqueous Na2SO4solutions at different scan rates of 2 mV·s-1(a)5 mV·s-1(b)and 10 mV·s-1(c)

3 Conclusions

Mn2O3plates and nanoparticle aggregates were synthesized through high temperature treatment of Mncontaining precursors obtained from the mixed systems of KMnO4and L-cysteine.Mn2O3phase could also be obtained afterthe heattreatmentofthe roomtemperature products in air at 120℃.It is found that Mn2O3colloid plates with sizes of 50～120 nm and Mn2O3colloidal/nanoparticles are single crystalline.The specific capacitance of Mn2O3samples is increased with the order of Mn2O3-RT,Mn2O3-120 and Mn2O3-150 at a low scan rate,where the morphology and size of the samples have strong effect on their capacitance.The formation mechanism of Mn2O3nanostructures and the relationship between Mn2O3nanostructures and their electrochemical properties are suggested.

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Mn2O3Nanomaterials:Facile Synthesis and Electrochemical Properties

ZHAO Dan1,2TAN Jin-Shan1JI Qian-Qian1,2ZHANG Jin-Tao3ZHAO Xiu-Song1,2,3GUO Pei-Zhi＊,1,2
(1Institute of Multifunctional Materials(IMM),Laboratory of New Fiber Materials and Modern Textile,The Growing Base for State Key Laboratory,Qingdao University,Qingdao,Shandong 266071)
(2College of Chemistry,Chemical Engineering and Environment,Qingdao University,Qingdao,Shandong 266071)(3Department of Chemical and Biomolecular Engineering,National University of Singapore,4 Engineering Drive 4,Singapore 117576)

The MnCO3with different structures was synthesized at room temperature or by hydrothermal method.The MnCO3phase obtained at room temperature could be transferred to Mn2O3plates by heat treatment at 600℃.In contrast,porous Mn2O3nanostructures can be obtained after the heat treatment of MnCO3precursors prepared by hydrothermal method.Interestingly,Mn2O3phase can be also formed by heat treatment of the MnCO3phase obtained at room temperature(Mn-RT)at 120℃.The products were characterized by means of XRD,SEM.The results clearly demonstrate a structure evolution from MnCO3precursors to Mn2O3structures on the completion of the reaction.The formation mechanism of the above materials was further investigated by TEM and FTIR.The capacitive properties of the Mn2O3materials were characterized by cyclic voltammetry.The results show that the morphologies and structures of Mn2O3samples play important roles on their capacitances.

Mn2O3;MnCO3;hydrothermal synthesis;capacitance

O614.7；O611.62

A

1001-4861(2010)05-0832-07

2009-11-06。收修改稿日期：2010-01-27。

國(guó)家自然科學(xué)基金(No.20803037)，山東省博士基金(No.2007BS04022)，山東省自然科學(xué)基金(No.ZR2009BM013)和泰山學(xué)者計(jì)劃資助。＊

。 E-mail：pzguo@qdu.edu.cn;會(huì)員登記號(hào)：S060004572P。

趙 丹，女，26歲，碩士研究生；研究方向：微納材料結(jié)構(gòu)與性能。