Content uploaded by Hamed Karkhanechi
Author content
All content in this area was uploaded by Hamed Karkhanechi on Nov 17, 2021
Content may be subject to copyright.
Membranes2021,11,884.https://doi.org/10.3390/membranes11110884www.mdpi.com/journal/membranes
Review
EffectiveParametersonFabricationandModificationofBraid
HollowFiberMembranes:AReview
AzadehNazif
1
,HamedKarkhanechi
1,
*,EhsanSaljoughi
1
,SeyedMahmoudMousavi
1
andHidetoMatsuyama
2,
*
1
DepartmentofChemicalEngineering,FacultyofEngineering,FerdowsiUniversityofMashhad,
Mashhad9177948974,Iran;azadehnazif@gmail.com(A.N.);saljoughi@um.ac.ir(E.S.);
mmousavi@um.ac.ir(S.M.M.)
2
ResearchCenterforMembraneandFilmTechnology,DepartmentofChemicalScienceandEngineering,
KobeUniversity,1‐1Rokkodai,Nada‐ku,Kobe657‐8501,Japan
*Correspondence:karkhanechi@um.ac.ir(H.K.);matuyama@kobe‐u.ac.jp(H.M.)
Abstract:Hollowfibermembranes(HFMs)possessdesiredpropertiessuchashighsurfacearea,
desirablefiltrationefficiency,highpackingdensityrelativetootherconfigurations.Nevertheless,
theyareoftenpossibletobreakordamageduringthehigh‐pressurecleaningandaerationprocess.
Recently,usingthebraidreinforcingassupportisrecommendedtoimprovethemechanical
strengthofHFMs.Thebraidhollowfibermembrane(BHFM)iscapableapplyunderhigherpres‐
sureconditions.Thisreviewinvestigatesthefabricationparametersandthemethodsfortheim‐
provementofBHFMperformance.
Keywords:braidhollowfibermembrane;fabricationparameters;mechanicalstrength;braid
reinforcing
1.Introduction
Membranetechnology,includingpolymericmembranes,isoneofthebest‐advanced
separationandtreatmentsystemsthathavebeenwidelyusedindifferentapplications
suchasdesalination,wastewatertreatment,oil/waterseparation,andwaterreuseappli‐
cations[1,2].Hollowfibermembranes(HFMs)possessdesiredandcompetitivead‐
vantagesrelativetoflat‐sheetmembranesformanymembraneseparationapplications
duetohighmembranesurfaceareapervolumeofamodule(e.g.,theratioofareaper
volumeisreported40m
2
/m
3
forflatsheetand170m
2
/m
3
forHFMs[3]).Theyalsohave
highpermeabilityandporosity,desirablefiltrationefficiency,propermechanicalproper‐
ties,self‐supportedstructureandcharacteristics,smallfootprint,highpackingdensity
relativetootherconfigurations,easeofhandlingandmaintenance[4–12].Duealsotothe
spacer‐freemodule,theassemblycostwillbereduced.Hollowfibermembraneshadbeen
widelyusedformicrofiltrationandultrafiltrationaloneorasthepretreatmentofnanofil‐
trationandreverseosmosisinseawaterdesalination,forwardosmosis,andmembrane
bioreactortothetreatmentofindustrialwastewater(suchasmedicine,food,andtextiles)
andgenerationofdrinkingwater.Hollowfibermembranesareoftenpossibletobreakor
damageduringhigh‐pressurecleaning,modulepreparation,aerationprocess.Itisdueto
sponge‐likeandasymmetricfinger‐likemorphologythatledtomakingbrittleandporous
structures.Hence,theirlifetimemayreducedespitetheirmanyadvantages[4,11,13].
Inordertodesignmembranestructure,lifetimepredictionandreliability,under‐
standing,andanalysisisimportanttoevaluatethemechanicalbehaviorunderactualop‐
eratingconditions.Mechanicalabrasionofmembranesarisingfromphysicalandchemi‐
caldamagebyharshfeedwater,fouling,chemicalcleaning,andback‐washingbring
aboutthereductioninmembranestrength[4,14].Generally,themechanicalpropertiesof
Citation:Nazif,A.;Karkhanechi,H.;
Saljoughi,E.;Mousavi,S.M.;
Matsuyama,H.EffectiveParameters
onFabricationandModificationof
BraidHollowFiberMembranes:A
Review.Membranes2021,11,884.
https://doi.org/10.3390/
membranes11110884
AcademicEditor:MariaGraziaDe
Angelis
Received:12October2021
Accepted:12November2021
Published:17November2021
Publisher’sNote:MDPIstaysneu‐
tralwithregardtojurisdictional
claimsinpublishedmapsandinstitu‐
tionalaffiliations.
Copyright:©2021bytheauthors.Li‐
censeeMDPI,Basel,Switzerland.
Thisarticleisanopenaccessarticle
distributedunderthetermsandcon‐
ditionsoftheCreativeCommonsAt‐
tribution(CCBY)license(https://cre‐
ativecommons.org/licenses/by/4.0/).
Membranes2021,11,8842of31
polymericflatsheetmembranesareimprovedbyapolyestersupportlayer.Thenonwo‐
venpolyesterpossessesstrongmechanicalstrengthcantoleratevigoroushydraulicim‐
pact[15–19].Hosseinietal.[15]utilizedpolyestersupportinordertoimprovetheme‐
chanicalstrengthinhighpressure.Recently,usingtubularbraid(orthreads/fabric)asre‐
inforcedsupportisproposedtoimprovethemechanicalstrengthofhollowfibermem‐
branes.Braid‐reinforcedhollowfibermembraneshaveattractedattentionandinterest
duetotheirlowcost,efficientseparation,relativelysimplepreparation,andhighmechan‐
icalproperties[6,7,11,20,21].Thistypeofhollowfibermembranepossessesasupreme
tensilestrength(contributestothelonglifetimeofthemembranes),andthustheycould
applyunderhigherpressureconditionsrelativetocommonhollowfibermembranes.A
braidhollowfibermembrane(BHFM)isfabricatedbycoatingathinfilmonthesurface
oftubularbraid(i.e.,reinforcedfiber).Thepresenceofbraidsupportincreasesthefluxof
ultrafiltration/microfiltrationduetothethinnerthicknessoftheselectivelayer,thanksto
toleratingrelativelyhigherpressurecomparedwiththetypicalHFM[4,21–24].Thefirst
studiesinreinforcedHFMsarerelatedtothepatents.Cooperetal.[25]introducedthe
conceptofbraidedmembraneforthefirsttime.Theycastthemembraneonasupporting
surfacesuchasfabric‐likematerialconsistingofmonofilamentmaterial(e.g.,polyesters,
nylon,rayon,polyolefin,Teflon,acrylic)withasmalldiameter.ZenonEnvironmentalInc.
producedatypeofhollowfibermembraneconsistingoftubularmacro‐poroussupport
andatubularsemipermeablethinfilmofthepolymer.Thepreparedbraidhollowfiber
membranecouldendureto10.3MPainhydrauliccompactionforces[26].
Thepeelingofthesurfacelayerfromthetubularbraidisthedrawbackofthebraid
hollowfibermembranesduetothermodynamicincompatibilitybetweenthesetwolayers
[21].Thebraidhollowfibermembranecansignificantlyenhancetheeffectiveareadueto
fewerstickingfiberstogetherintheassembledmodule[27].Thebraidsupportabsorbs
themoleculesofwaterduetotheporousstructure.ThethinseparationlayeroftheBHFM
alsocontributedtothewaterfluxenhancementbecauseoflowerthicknesscomparedto
self‐supportHFMs[24].Chenetal.[28]reportedthatthefluxofbraidPMIA‐BHFMswas
higherthanthePMIA‐HFMs.ItisduetothePMIA‐BHFMscontaininganinnerlayerwith
arelativelyporousstructurethatleadstoareductioninmembraneresistanceforwater
transfer.TheBHFMswiththedenseoutersurfacecanpreventtheadsorptionoffoulants
andthepore‐blockageintheinnerporesofthemembrane.Therefore,theoccurredfouling
isformingthecakelayertype,caneasilyremovebywashing,whiletheopenporesofthe
HFMeasilyadsorbedthemoleculesofprotein.Inthiscase,theporesofthemembrane
willbeblocked.Thistypeoffoulingisirreversibleandhardlyeliminatedthroughwater
washing.Therefore,thecaseofirreversiblefoulingrequiredacombinationofchemical
cleaningandback‐washing[29].
BHFMsarefabricatedbytwospinningmethods:electrospinningmethodandnon–
solvent‐inducedphaseinversion(NIPS)basedonthedry‐wetspinning.Basedonthelit‐
erature,membranespreparedbytheNIPSmethodbasedonthedry‐wetspinningprocess
aremorecommonandhavehigherwaterfluxduetothinseparationlayers[24].Asshown
inFigure1,thetubebraid(liketheborefluidinjectioninthefabricationofcommon
HFMs)isinsertedthroughthemiddleofthespinneret.Thenthepolymersolutionisuni‐
formlycoatedonthebraidtube.Thepreparedbraidhollowfibermembraneisimmersed
intoacoagulationbath,anditisfinallywounduponthedrum[4,30].
Membranes2021,11,8843of31
Figure1.Schematicillustrationofthefabricationofbraid‐reinforcedhollowfibermembranes(BHFM).
Recently,theelectrospinningmethodhasbeenattractedmuchattentiontogenerat‐
ingpolymerfibersintherangeofseveralmicronstonanometerdiameter(50nmand10
μm).Desirableproperties(functionality,porosity,weight,andstrength)canbeachieved
bythetypeofpolymerandefficientcontrolofoperatingconditions.Alargespecificarea,
ahighratiooflengthtodiameter,anduniformporesizedistributioncanbeachievedby
theelectrospinningmethod.Thebaseofthismethodisahigh‐voltageelectricfieldforthe
productionofnanofibersfromapolymericstreamthatisreleasedbyanozzlesystem.This
techniquecontributestoproducingofultrathinlayersfromdifferentfibers,particles,and
polymers.Thegeneratedfibersfromthismethodareaffectedbypolymericsolutionprop‐
erties(concentrationandthemolecularweightofpolymer),environmentalconditions
(humidityandroomtemperature),andoperationparameters(solutionflowrate,applied
voltage,andtip‐collectordistance).Intheelectrospinningmethod,thesyringefillswitha
polymericsolution,thenpumpstothenozzleataspecifiedflowrate.Thebraidlayeris
locatedonathincylindricalthatisjoinedtotherotatingshaft.Thefiberswillbegenerated
bycoatingthepolymersolutiononthebraidlayerbyapplyingtheelectricpowertothe
nozzle(Figure2)[31,32].Aslanetal.[31]fabricatedtubularelectrospunnanofibermem‐
branesasmicrofiltrationmembranes.Polyacrylonitrile(PAN)nanofiberscoatedonthe
braidedrope.Themorphologyandfiltrationcharacterizationshowedexcellentproperties
intermsofcross‐sectionthickness,waterflux,turbidity,porosity,hydrophilicity,anduni‐
formdistributionofporesize.
Membranes2021,11,8844of31
Figure2.Schematicdiagramofanelectrospinningsetup[31].
Kimetal.[5]introducedpatternedmorphology(prismandpyramid)tothesurface
ofBHFM,asshowninFigure3,byaimingtodeclinethefoulinginMBRforwastewater
treatment.Theinjectionrateofthenon–solventmainlyaffectedthemorphologyofthe
membranes.Uniformdistributionofmacrovoidsobservedforthehighinjectionrateon
thetotalcross‐sectionsurface.Inalowinjectionrate,adenseandthickpolymerfilmwas
formedinwardandoutwardofthebraid,andlargemacro‐voidswerecreatedexternal
sideofthepolymerfilminthevicinityofthebraid.Thisobservationcanbeexplained
basedontheinfiltrationofthenon‐solvent.Inalowinjectionrate,thenon‐solventwould
inducephaseinversioninsideandnearthebraidrelativetoinfiltrationfurthertothe
braid.Hence,thebulkofthepresentpolymeroutsidethebraiddiffusestowardthebraid
thatleadingtocoagulation.Therefore,adenseandthickpolymerfilmwasformedinside
ornearthebraid,andlargemacrovoidswerecreatedoutsidethebraidbecauseofan
insufficientcontentofthepolymer.Inahighinjectionrate,thenon‐solventdiffuses
quicklyinthetotalareaofthepolymericsolution.Hence,phaseinversionwouldhappen
withmorespeedalloverthepolymersolutionrelativetothemigrationofthepolymerto
thebraid.Therefore,amoreuniformdistributionofmacrovoidsiscreated.
Figure3.TheschematicofpatternedBHFM(b)lowinjectionrateofnon‐solvent(c)highinjection
rateofnon‐solvent[5].
ThereisalimitedamountofpapersthatreviewedtheBHFMs[33,34].Wespecially
reviewedtheeffectivefabricationparameters,modification,andperformanceofbraid
hollowfibermembranesinthedifferentapplications.Hence,thetypeandcontentofpol‐
ymer,additive,themethodsforincreasinginterfacialbondingbetweenthebraidandsep‐
arationlayer,andotherefficientparametersarediscussed.
Membranes2021,11,8845of31
2.EffectiveFabricationParameters
Dopeandbraidcompositionsuchastypeandconcentrationofpolymerandadditive,
fabricationparameters,andoperationalconditionsplayvitalrolesinthesuccessofthe
BHFMfordifferentapplications.Accordingly,theresearchersinvestigatedthevarious
aspectstoenhancetheperformanceofBHFMsfordifferentapplications.
2.1.TypeofPolymerinaDopeSolution
Theselectionofmaterialisanessentialfactorintheachievementofdesiredperfor‐
manceinmembraneapplication.Polymericmembranesarethemostusedmembranesfor
differentapplicationswithhighdesignflexibility[35].Severalpolymershavebeenem‐
ployedforthepreparationofBHFM,suchaspolyacrylonitrile(PAN),poly(vinylchlo‐
ride)(PVC),celluloseacetate(CA),polysulfone(PSf),andpolyvinylidenedifluoride
(PVDF).Table1providesthepropertiesofpolymersusedforthepreparationofBHFM.
Table1presenttheusedpolymersforBHFMandtheirproperties.
PVCisoneoftheusualandpromisingpolymersformembraneapplication.How‐
ever,foulingproblemscanrestrictthePVCmembranesinwaterapplicationowingto
theirhydrophobicnature.TheblendingofanamphiphiliccopolymerandPVCinthedope
solutionisoneofthemethodsthatcanovercometheantifoulingproperties.Thehydro‐
philicpartoftheamphiphiliccopolymerisconnectedtothemembranesurface,which
leadstoamembranewithgoodantifoulingproperties.Thehydrophobicsectioncreates
goodcompatibilitywiththemembranematrixandincreasesthemaintenanceofcopoly‐
merinthemembranematrix.Zhouetal.[36]preparedtheBHFM‐purePVCandblended
BHFMwithdifferentblendratiosofPVC/copolymer.Theburstingstrengthandtensile
strengthofBHFMwerehigherthan2.1and170MPa,respectively,whichwerelargerthan
thoseoftheself‐supportingHFMs.
Copolymers,includingpoly(ethyleneoxide)(PEO)orpoly(ethyleneglycol)(PEG)
chains,cancreateahydrationlayer,preventingthebindingofthefoulantsmoleculesto
thesurfaceofthemembrane.However,PEG‐basedcopolymerissuggestedtoimprove
theantifoulingpropertiesandhydrophilicityofPVCmembranes.SincePEGiscatego‐
rizedinsoftpolymers,increasingthePEGcontentinthedopesolutioncanreducethe
mechanicalstrength.Henceitcanlimitthemembraneapplicationinpracticalwastewater
treatmentduetodamagingthemembranestructureduringthebackflushprocessoraer‐
ation[36].Therefore,theoptimizationofPEGcontentisessentialinordertoobtainanti‐
foulingpropertiesanddesirablemechanicalstrengthforpracticalapplication.Zhouetal.
[36]usedamphiphiliccopolymerpoly(vinylchloride‐co‐poly(ethyleneglycol)methyl
ethermethacrylate)(poly(VC‐co‐PEGMA))toendowhydrophilicitytoPVCbraidhollow
fibermembrane.Considerableimprovementwasobservedinantifoulingpropertiesand
hydrophilicitywhenthecopolymer/PVCblendingratiointhecoatingsolutionwasused
inoptimumcontent.
PANhollowfibermembraneshavebeenwidelyutilizedinpervaporation,thetreat‐
mentofindustrialwastewater,andenzymeimmobilizationapplications.Fabricationof
thesubstrateforcompositemembranesisanotherPANapplicationduetofavorableprop‐
erties.LowmechanicalstabilitylimitsPANapplicationinmicro/ultrafiltrationandMBR
systems[7].Quanetal.[7]preparedthePAN‐BHFMbycoatingPANsolutionsonthe
PET(Polyethyleneterephthalate)andPANtwo‐dimensionalbraidsurface.ThePAN‐
BHFMbasedonthePANbraidhadexcellentmechanicalpropertiesduetogoodinterfa‐
cialbondingbetweenthepolymerandthebraid.Itwaspossessedatensilestrengthhigher
than80MPa.
Theexcellentmechanicalstrengthandotheradvantages(asshowninTable1)ofPSf
membranesuggestthisisagoodcandidateforwastewatertreatmentsystems,textiledye‐
ing,anddesalination.PSfmembranesrequiresurfacemodificationinordertoenhance
hydrophilicityandwaterpermeation[24].Theincorporationofhydrophilicnanoparticles
Membranes2021,11,8846of31
inthePSfmembranecanimproveantifoulingpropertiesandincreasethefluxrate.Peech‐
manietal.[24]fabricatedhybridPSf/zincoxide(ZnO)BHFMstoincreasefluxandim‐
provehydrophilicity.TheBHFMswerepreparedwithdifferentconcentrationsofZnO
nanoparticles.TheZnOnanoparticlesleadtoanincreaseintheoverallfluxandabsorp‐
tionofwatermoleculesontothemembranesurfaceduetohydrophilicnatureandwater‐
lovingproperties(absorptionofhydroxylgroups).Increasingthehydrophilicityofthe
membranesurfaceleadstodecreasingtheinteractionsbetweenorganicmattersandthe
membranesurface.Hence,lessfoulingbyorganicfoulantshappensonthehydrophilic
membranes.
CAmembranesareanothertypeofpolymermembranethatplaysasignificantrole
inmembraneseparationduetofavorablepropertiesbasedonTable1.Despitethegood
propertiesofCAhollowfibermembranes,theweakmechanicalstrengthlimitedtheirus‐
ageinpracticalapplicationssuchasmembranebioreactors.TheHFMinthesubmerged
MBRcaneasilybebrokenordamagedduringtheback‐washingprocessoraeratedair‐
flow.Hence,itisrequiredthistypeofmembranepreparedwithhighmechanicalproper‐
ties.CAmembraneasahydrophilicmembraneshowedthehighperformanceforanti‐
foulingpropertieswhenfacedwithBSAsolution.ThedenseoutersurfaceofBHFMcould
avoidorlimittheblockingoftheinnerpore.Hence,thecreatedfoulingismainlydueto
adsorptionand/ordepositionofpollutantsonthemembranesurface,whichiseasilyelim‐
inatedbywaterwashing[21].
OneofthemainaromaticpolyamidesisPoly(m‐phenyleneisophthalamide)(PMIA)
withhydrophilicproperties,goodmechanicalproperties,excellentthermalstabilitydue
tothehydrogenbondnetwork,andaramidgroups.Thispolymeriswidelyusedfornan‐
ofibersproductionandinwatertreatmentapplications.Chenetal.,preparedPMIAhol‐
lowfibermembranescontainingseparationlayersandreinforcedbraids.ThePMIA‐
BHFMexhibitedgreatantifoulingpropertyrelativetoPVDFmembranes.ThePMIA
membranesexhibitedahighernegativitychargerelativetothePVDFmembranesdueto
thestrongpolaramidegroups(–NH–CO–)inthemacromolecularchainofPMIA.These
groupsleadtocreatingstrongelectronegativityandsuperiorhydrophilicityPMIAmem‐
branes.Thesepropertiesarethemaingoaltoimprovetheantifoulingproperty[28].
Membranes2021,11,8847of31
Table1.Used‐polymersforBHFMandtheirproperties.
PolymerChemicalStructure.Advantages Disadvantages/ImprovementApproachApplication Ref.
PAN
- Lowprice
- Excellent ag‐
ing‐resistance
- Highhydro‐
philicity
- Goodstability
- Goodsolvent
resistance
- Lowmechanicalstability
Water,municipal,
andindustrial
wastewatertreat‐
ment
[7,31]
PVC
- Excellentme‐
chanicalstrength
- Highcorrosion
resistance
- Lowcost
- Hydrophobicnature/Usingam‐
phiphiliccopolymer
UltrafiltrationBHFM
forwastewatertreat‐
ment
[36]
PSf
- Excellentme‐
chanicalstrength
- StabilityatpH
levelsfrom2to13
- Excellentre‐
sistancetocaustic
- Goodre‐
sistancetomoder‐
atechlorine
- Operatingat
hightemperature
andpressure
- Hydrophobicnature/Incorporationof
zincoxide(ZnO)
Wastewater
treatment[24]
Membranes2021,11,8848of31
CA
- Goodfilm
forming
- Relativelylow
cost
- Highflux
- Goodtough‐
ness
- Biocompatibil‐
ity
- Poormechanicalproperty/Usinghomo‐
geneousbraidreinforced
Wastewater
treatment[21,37]
PVDF
- Goodhydro‐
phobicproperty
[38]
- Semi‐crystal‐
linepolymer
- Goodmechani‐
calstrength
- Stability
againstvigorous
chemicals
- Goodthermal
stability
- dramaticallydecreasingofhydrophobi‐
cityincontinuoususe/blendingmethod
forimprovingthehydrophobicity(Gra‐
phene)[38]
- hydrophobicproperty[30]
oil/waterseparation
[38]
wastewater
treatment[30]
[38–42]
PMIA
- Highthermal
stability
- Excellentme‐
chanicalproper‐
ties
- Hydrophilic
property
NAwastewater
treatment[28]
Membranes2021,11,8849of31
PU
- Biodegradabil‐
ity
- Biocompatibil‐
ity
- Lowcost
NAoil/waterseparation[43]
PAN:Polyacrylonitrile;PVC:Polyvinylchloride;PSf:Polysoulfone;CA:Celluloseacetate;PVDF:Polyvinylidenefluoride;PMIA:Poly(m‐phenyleneisophthalamide);Pu:
polyurethane;NA:notapplicable.
Membranes2021,11,88410of31
2.2.TheEffectofPolymerConcentration
Generally,thepolymerconcentrationhasasignificanteffectonmembraneperfor‐
manceandstructure.Asthepolymerconcentrationisincreasedinthedopesolutions,the
finger‐likeporestructureisgraduallyconvertedtoasponge‐likeporestructure,andthe
porediameterbecomessmaller.AscanalsobeseeninFigure4,thehigherpolymercon‐
centrationcausestheformationofthedenserandthickerskinlayer.Incontrast,thelooser
structureisreportedforthemembranecontaininglowpolymerconcentration.Thehigh
polymerconcentrationleadstoincreasingtheviscosityofpolymersolution.Therefore,
therateofdiffusionisreducedbetweensolventandinthephaseinversionprocess.In‐
stantaneousdemixingcreatesmembraneswithaporouslayerandafinger‐likestructure,
whereasdelayeddemixingresultsinmembraneswithdensestructuresandsponge‐like
pores.Thedensandsmoothstructureandsmallporesizeofthemembranesurfacecause
animprovementtotheantifoulingabilityandseparationpropertyofthemembrane,
thoughthefluxwillbereduced.Therejectionismoredependentonthedensityofthe
separationlayercomparedtothestructureofthecross‐section[28,37,44].Fanetal.[21]
reportedthattherejectionofmembranewiththelowconcentrationofCAhadminimum
rejectionduetobigsizepores.Theyalsoobservedanincreaseinpolymerconcentration
indopesolutionleadtothecreationofasurfacewithsmoothanddenseproperties.The
burstingandtensilestrengthsalsoincreasedduetointerfacialbondingbetweentubular
braidandseparationlayer.Zhangetal.[45]observedtheBSArejectionforBHFMwas
higherthantheHFM.ItwasduetothedenserskinlayerandsmallerporesizeinBHFM
relativetoHFM.Theporesizeisanessentialfactorthataffectsmembranepermeability.
AsshowninFigure5,theincreaseinpolymerconcentrationindopesolutionleadsto
decreasingofpurewaterfluxandincreasingtherejectionduetolowerporosityandpore
sizeofthemembrane[7,40,46].
Thecontactanglebetweenthebraidandthecoatingsolutionincreasedwhenthe
polymerconcentrationincreased.Itisduetotheviscosityofpolymersolutionenhanced
withtheincreaseinpolymerconcentration;hence,thesolutionfluiditywillbereduced
[7,40,46].
BasedontheinvestigationofChenetal.[28],theantifoulingproperties(performance
andfluxrecoveryratio)forPMIABHFMwerebetterinahigherconcentrationofpolymer.
Itmaybeduetothepresenceofstrongpolargroups(−NH−CO)inthemacromolecular
chainofpolymerthatleadstocreatingexcellenthydrophilicityandstrongelectronegativ‐
ity.Theotherreasonisthedenseoutersurfaceandsmallporesizeinthehighconcentra‐
tionofpolymerthatavoidstheporeblockageofinnerpores.Hence,thefoulingandform‐
ingofthecakelayermainlycreateonthemembranesurfacethatiseasilyremovedinthe
cleaningprocess.
Figure4.TheeffectofpolymerconcentrationonBHFMstructure(b1)5%,(b2)8%,(b3)10%,and(b4)15%[28].
Membranes2021,11,88411of31
Figure5.Effectsofpolymerconcentrationonthe(a)purewaterfluxand(b)proteinrejection[28].
Asmentioned,thepresenceofthebraidreinforcementleadstonotableenhancement
ofmechanicalproperties.Forexample,Liuetal.[46]observedthatthetensilestrengthfor
amembranewiththreethreadswasmorethansixtimesrelativetothemembranewithout
thread.Thereisthephysicalandchemicalforcebetweentheinterfaceofpolymerand
braidlayer.Thephysicalforceconsistsofconglutinationandwedge,andchemicalforce
createdbythechemicalbonds.Thewettabilityofbraidbypolymersolutionisthemain
factorthataffectstheinteractionforcebetweentwolayers.Thecontactanglebetweenpol‐
ymersolutionandbraidmustbesmalltoobtainsufficientcontactingandwettingbetween
them.Withanincreaseinthepolymerconcentration,theviscosityandsurfacetensionis
increased.TheburstpressureofHFMisaresistingcapabilityinaradialdirectionmainly
determinedbyforcebetweenthemoleculechainsofpolymers.Thisparameter,asacritical
parameterinthecleaningprocess,representstheinterfacialbondingstateofBHFMtoa
certainextent.Inthepracticalapplication,theoperatingpressureisrestrictedbytheburst
pressureduetothesmalleffectofbraidthreadontheradialdirectionpersistence[21,28].
ThehighburstingstrengthwouldrestricttheharmofBHFMSintheback‐washingpro‐
cess.Itisenhancedwiththeincreaseinpolymerconcentrationinthedopesolutiondue
tothesuperiormechanicalstrengthoftheseparationlayerinhigherpolymerconcentra‐
tions.Thereisatighterstackofmoleculechainsinthemembranewithhigherpolymer
concentration.Hence,theyhaveahigherburstpressure.Thereisastrikingcorrelation
betweentheburstpressureandoperationforthenormalHFM.However,addingbraid
threadsleadstoanisotropyinthetransversalandlongitudinaldirections,sotherelation‐
shipissmallforBHFM.Themembranematerialandstructureeffectonburstpressure
andtensilestrengthisinfluencedbybraidthread.
Fanetal.[37]observedthatanincreaseinthepolymerconcentration(from6to14
wt.%)inthedopesolutionwascontributedtotheenhancementofthetensilestrengthof
CA‐BHFM(from11to14MPa).BasedonastudybyChenetal.[28],themechanical
strengthisdominantlygovernedthroughthereinforcedbraids.Thebreakingelongation
andtensilestrengthwereapproximatelysimilartothetensilestrengthofthebraids.The
burstingstrengthandinitialmodulusenhancedwiththeincreaseinthepolymerconcen‐
trationbecausetheseparationlayerwasfirmlybondedwiththebraidlayerthathindered
thedeformationofthebraidlayer.Theseparationlayeralsohadabettermechanical
strengthinhigherpolymerconcentrations.
Membranes2021,11,88412of31
2.3.EffectofAdditives
Thepresenceofadditivesinbulkoronthesurfacemembraneisoneoftheeffective
approachestoimprovemembraneperformancethroughthemodificationofroughness,
hydrophilicity,poresize,andsurfacecharge[15].Zhouetal.[36]fabricatedtheBHFMby
blendingPVCanddifferentblendratiosofpoly(VC‐co‐PEGMA)copolymer.Therewasa
highinterfacialbondingstrengthbetweenthePET‐braidandpolymersolution.Although,
thecopolymerscontainedPEGdemonstratethestrongabilityofpore‐forming,which
leadstocreatinglargeporesandporosityenhancement.Thepreparedmembraneexhib‐
itedantifoulingresistanceandhighmechanicalproperties.ThetensilestrengthofPVC‐
BHFMwassignificantlyhigherthanPVC‐HFM.Themembranehydrophilicityincreased
withincreasingthecopolymerconcentrationofthedopesolution.Highhydrophilicity
bringsaboutafasterdemixingprocessanddiffusionofwaterintothepolymersolution
duringthemembraneformation.Hence,alargerporesizewillcreateintheselectivelayer
comparedwithlowhydrophilicity.Theoptimizationofcopolymercontentisnecessary
becauseanincreaseincopolymercontentbasedonPEGinpolymersolutionleadstoa
reductioninmechanicalstrengthofmembraneduetothePEGsoftness.
Peechmanietal.[24]showedthatthepresenceofZnOnanoparticlesindopesolution
causeddelay‐demixingbetweennon–solventandsolventduetoviscosityenhancement.
Thus,theformationofmacrovoidswasconsequentlyincreased.Byincreasingtheconcen‐
trationofnanoparticles,themacrovoidsanddensespongestructureandconsequently
higherpermeationincreasednearthebraidlayer.Itisduetothehydrophilicnanoparticles
thatcontributetothefastermovingofwatermoleculesintothemembranematrixrelative
tothedemixingratebetweennon–solventandsolventduringthephaseinversionprocess.
TheBSArejectionandwaterfluxwerehighercontentsinthehighestcontentofZnOcom‐
paredtoothermembranes.ItisoccurredbecauseofthehydroxylgroupofZnOnanopar‐
ticlesintheselectivelayerthatreceivesmorewatermolecules.Thestrongelectronegativ‐
ityofnanoparticlesalsoresultsinavoidingthedepositionofBSAproteinsintheselective
layer.
Lanetal.[47]fabricatedaBHFMconsistingofPVDFasabasepolymerandPETa
woventubalasasupportlayer.TheyusedTiO2nanoparticlesfortheimprovementof
hydrophilicity.Thepreparedmembraneshaddesirablepropertiesintermsofthefiltra‐
tionareaandmechanicalstrengthrelativetoconventionalHFM.TheBHFMcontaining
1%TiO2hadthebestantifoulingproperty,thehighestflux,andthelowestfluxdecline
rate.
Haoetal.[38]preparedaPET‐braid‐reinforcedPVDFhollowfibermembranewith
differentconcentrationsofgraphenetoincreasethemembranehydrophobicityinoil‐wa‐
terseparationapplication.ThePETtubularbraidswerecoatedwithaPVDF/graphene
solution.Theviscositiesofpolymersolutionsfirstincreasedandthenreducedwithan
increaseingraphenecontents.Theviscosityofpolymersolutionvariedwhentheshear
rateincreasedandshowedthepropertiesofapseudoplasticfluid.Thepolymersolution
withoutgraphenehadalowviscositythatrepresentednoconsiderablechangewiththe
enhancementofshearrate.Theviscosityofthepolymersolutionchangedclearlyforthe
membranewiththehighestamountofgraphene.Itisduetographenebeingalaminated
andrigidsubstancewithahighYoung’smodulus.Inalowshearrate,thepresenceof
toughgrapheneincreasedtheflowresistanceofpolymersolution.Withtheincreasein
shearrateandexceedingfromaspecifiedamount,theeffectofflowresistanceforgra‐
pheneslowlyweakened,andtheviscosityofthepolymersolutionwasconsequentlyde‐
creased.Haoetal.observedsmallmeanporesizeandthefluctuationinthicknessofthe
selectivelayerinthemaximumconcentrationofgrapheneduetothehighviscosityand
lowfluidityofpolymersolution.Therandomdistributionofgraphenesheetsintheselec‐
tivelayersofBHFMsresultedincreatingamembranewithastableporestructuredueto
therigidnatureofthegraphenesheets.Wuetal.[43]fabricatedaPU/grapheneBHFM
basedonPETbraidedforoil/waterseparation.Thepreparedmembranesshowedgood
Membranes2021,11,88413of31
lipophilicpropertiesbasedoncontactangleresults.Goodselectivityforoil‐watersepara‐
tionwasalsoachieved.
Liuetal.[29]investigatedtheeffectofmolecularweightsofpolyethyleneglycolon
thestructureandperformanceofhomogenousreinforcedPVC‐BHFMs.Thepresenceof
PEGwithhighmolecularweightleadstoincreasingthethicknessoftheseparationlayer
becauseoftheenhancementofsolutionviscosity.Thehighviscosityrestrictstheexchange
ofthesolventandnon–solvent.ThehighmolecularweightofPEGcreatedabiggerfinger‐
like,smoothoutersurfaceandcompactskinlayerrelativetothelowmolecularweightof
PEG.TherejectionofBSAproteinincreased,andtheporosityreducedwhenthemolecular
weightofPEGwasenhanced.Itisduetoincreasingthethicknessoftheseparationlayer
andformingthedenseouterlayerwiththeincreaseinthemolecularweightoftheaddi‐
tive.ItisnotablethatthemolecularweightofPEGdidnotinfluencethemechanicalprop‐
ertiesofpreparedmembranes.
2.4.EffectofBraidComposition
Tworeinforcingmethodsarereportedintheliteratureinordertoimprovetheim‐
provementofmechanicalpropertiesofHFMs:fibersreinforcedandporousmatrixmem‐
branereinforcedassupport.Thefibersreinforcedmethodislow‐costandstraightfor‐
ward.Itcouldbedonebythetubularbraidreinforcedbasedonthereinforcementshape
andthecontinuousfiber‐reinforcedmethod.Leeetal.[48,49]fabricatedabraid‐reinforced
compositeHFMconsistingofatubularbraidwithmultifilament.Themultifilamentis
formedfrommonofilamentswithafinenessof0.01to0.4denier.Thesurfaceareabetween
thepolymerthinfilmandtubularbraidisincreasedbecausethefinenessofthemonofil‐
amentsissmall.Hence,thepeelingstrengthofthepolymerthinfilmandtubularbraidis
excellent,aswellasthemembranewettabilityisexcellentbecauseofthecapillarytube
phenomenon.
Inthesecondmethod,theporousmatrixmembraneasthereinforcementisfirstly
preparedbymelt‐spinningcold‐stretchingorthermallyinducedphaseseparation;then,
thesurfacecoatingiscarried.Thismethodisapproximatelyhighcostandcomplex[6].
Liuetal.[46]fabricatedcontinuouspolyesterthreadsPVDF‐HFMbyincorporatingPET
threadsinthesupportlayerintheaxialdirection.Theyfoundthatthetensilestrengthof
theBHFMsimprovedupto10MPabytheincreasingofPETthreadsnumber.ThePET
threadshadloweffectsontheseparationpropertiesofthemembrane,butthetensile
strengthofthemembranewasincreased.
Bothpureandhybridcompositionforthebraidisreportedintheliterature.Fanet
al.[37]preparedahomogeneousBHFMwhichconsistedofaCAforthebraidandsepa‐
rationlayer.Thepreparedmembraneindicatedagoodinterfacialbondingstate,butthe
CAfibersinthebraidtendtobeswollenandsicktogether,whichdecreasesthepermea‐
bilityandfluxofthemembrane.Hybridbraidleadstochangingporousstructure,en‐
hancesthemembraneseparationproperties,andreducesthedrawbackofthehomoge‐
nousmethod.Fanetal.[21]preparedaBHFMbasedonahybridbraid.Thehybridbraid
consistsofCAandPAN.ThepresenceofPANfiberinhybridcompositionovercamethe
CAfiber’sswellingandreductioninpermeability.Thetensilestrengthofprepared
BHFMsincreasedfrom16.0MPato62.9MPabyoptimizingtheCA/PANratiointhebraid
composition.TheburstingstrengthwasenhancedwhenCAfiberproportionincreasedin
thebraid.Liuetal.[6]fabricatedaheterogeneousBHFMconsistingofahybridbraid(PET
andPAN)andacoatinglayerofPVC.Thepreparedmembranehadadesirableinterfacial
bondingstateandtensilestrengthrelativetothemembranecontainingpurePANorPET
braid.ItwasalsoobservedthatthetensilestrengthdecreasedwhenPANfilamentsin‐
creasedinthecompositionofthehybridtubularbraid.
Quanetal.[7]investigatedtheeffectoftwotypesofbraid(PANandPET)onmem‐
braneperformance.ThemembranewaspreparedbasedonPANbraidasahomogenous
membraneandPETbraidasaheterogeneousmembrane.Theirresultsshowedthatthe
interfacialbondingstateofthePANmembranewasbetterthanthePETmembrane.The
Membranes2021,11,88414of31
contactanglebetweenthebraidandthecoatingsolutionwaslowerforthePANmem‐
brane.ThetensilestrengthandpurewaterfluxofthePETmembranewerehighercom‐
paredtothePANmembrane.
Table2summarizesthestudiesforBHFMsbasedonhybridcompositionandpure‐
compositionbraid.ThePETbraidisusedinmostoftheBHFMinthepure‐composition
braid.PVP(Polyvinylpyrrolidone)orPEGisgenerallypresentindopesolutionaspore
former.Thepresenceofadditivesimprovestheseparationpropertyandwaterfluxinop‐
timumcontent.
2.5.ThinFilmComposite:BraidHollowFiberMembranes(TFC‐BHFM)
SomestudieshaveconcernedforimprovingpropertiesandperformanceofTFC‐
BHFMbyoptimizationoffabricationparameterssuchassoakingtime,monomerratios,
reactiontime,andmonomerconcentrationinorganicoraqueoussolution.
2.5.1.TheEffectofMonomerConcentrationonTFC‐BHFM
Thesurfaceproperties(e.g.,hydrophilicity,functionalgroups,crosslinkingofmon‐
omers)andstructure(e.g.,thickness,poredimension,androughness)oftheselective
layerdirectlyaffectonthemembraneperformance.Thus,itisnecessarythefundamental
understandingoftheinfluenceofdifferentmonomersforthepreparationofhigh‐perfor‐
mancemembraneswithdesirablestructures[50].
Xiaetal.[10]investigatedtheTFC‐BHFMswithdifferentmonomerconcentrations
(PIP(piperazine)andTMC(trimesoylchloride)).TheyfabricatedtheNFmembranethat
exhibitedhighstrengthatpressuresupto70psiwithoutfractureandcreatedtheintegrity
intheBHFMatpressurestypicallynotutilizedforfibersofthissizebyusingbraid‐rein‐
forcedandoptimizationofmonomerconcentration.ThepreparedTFC‐BHFMcouldbe
usedforprocessesthatsaltselectivityisrequired.Itwasreportedthatthewaterpermea‐
tioninthelowconcentrationofTMCwashigherincomparisonwiththelowconcentra‐
tionforbothmonomers(i.e.,PIPandTMC).Itcanbeexplainedthatthemembranedefects
arereduced,oritmaybeduetotheincreasingofthethicknessordensityoftheselective
layerinahighermonomerconcentration.Thedifferentresultsobservedfromthistrend
inthepreparedmembraneswiththehighestcontentofPIPandminimumcontentofTMC.
ItisprobablyduetocreatingathickbarrierfilminthelowestTMCconcentrationinorder
tostopthereactionrapidly.ThehighTMCconcentrationshadapositiveeffectonMgSO4
rejection.Thedifferentconcentrationsofaminegroupstypicallycausethevariousperme‐
ation,whichislikelyduetoreducingtheporesizeofthemembrane.Figure6showsthe
reactionbetweenTMCandPIPtoformpolyamideasaselectivelayer.
Figure6.ThereactionbetweenPIPandTMCforpolyamideformation[51].
2.5.2.EffectofSoakingandReactionTimeinTFC‐BHFMPreparation
ThesoakingofthesupportlayerisastepofTFC‐BHFMfabricationthatimpactsig‐
nificantlyontheperformanceofpreparedTFC‐BHFM.Ununiformedwettingmayleadto
thedecreasingofmembraneselectivity.UsingthePVDFsupportinthefabricationofthe
TFCmembraneisamainchallengeduetoitshydrophobicnatureandwettingdifficulty
[10,52].Xiaetal.[10]preparedtheTFC‐BHFMswithdifferentsoakingtimes.Thevisual
propertieswerenotchangedbasedonthevariationofsoakingtime.Anincreaseinthe
Membranes2021,11,88415of31
soakingtimeleadstodecreasinginpurewaterpermeability,whilethesaltrejectionfirstly
increasesandthendecreases.Theseresultsareduetoformingauniformselectivelayer
withfewerdefectsafterentirelywettingbythePIPsolutionatthelongersoakingtime.
Themodificationofsupportsurfacethroughplasma,coatingwithhydrophilicpoly‐
mers(e.g.,PANandPVA),wettingofmembranebyinvertthesequencesoakinginthe
organicphaseandthenimmersionintheaqueousaminephasearethemethodsforwet‐
tabilityimprovementoftheofPVDFsupportthatinvestigatedbyresearchers[10].
Reactiontimeisacrucialfactorininterfacialpolymerizationthataffectsthestructure
ofthecoatinglayerandspecifiestheextentofpolymerizationbetweenthemonomers[53].
Turkenetal.[51]fabricatedreinforcedTFC‐HFNFmembranes.Theyselectedtherein‐
forcedPSfultrafiltrationasasupportandpolyamidelayerasaselectivelayerthatwas
preparedfromtrimesoylchloride(organicphases)andpiperazine(aqueousphases)mon‐
omers.TheimmersiontimeofTMCwasoptimizedinfixedconcentrationsofTMCand
PIPtoachievethehighestmembraneperformance.Thehydrophilicityofthemembrane
increasedbyenhancementofthecrosslinkingdegreeofthepolyamidelayerandtheTMC
reactiontime.Turkenetal.[51]reportedthehigherspecificpermeatefluxinhigherTMC
reactiontimesforreinforced‐TFC‐NFmembranes.Thehydrophilicityofthemembrane
enhancedwhenthereactiontimeofTMCincreased.Itisknownthatwhenthecrosslink‐
ingdegreeofthepolyamidelayerisincreased,theformationofthemembranewitha
highlyhydrophilicnatureisenhanced.Thepresenceofthepolyamidelayeronthesurface
ofthemembraneleadstothecreatingofaTFCsurfacewithmorenegativelycharged.The
negativechargeofthemembranesurfacewasdecreasedwhenthereactiontimeofTMC
increased.Theformationof−COOHgroupsismoreinshortreactiontimeofTMC.Since
thetimeofTMCreactionisoneoftheeffectiveparametersincrosslinkingdegreeofinter‐
facialpolymerization;hence,itinfluencedthesaltrejectionandwaterflux.Theformation
oftheamidegroupisavitalsignforthecrosslinkingdegreeofmonomer,thehydrolyzing
ofacylchloride,andfilmformationandgrowth.DuringthecontinuousreactionofTMC
andPIP,itisexpectedthattheamountof−C=Ogroupsincreasedinthemembranes.The
presenceofthemore−C=Ogroupindicatedmorereactionbetweenthemonomers.The
existenceofthe−OHgroupisasignofthehydrolysisofTMC.Atthebeginningofthe
reaction,thewaterdiffusionintothemembranematrixfacilitatesthehydrolysisofTMC.
Thehydrolysisofthemembranebytheaqueousphaseattheinitialstage(orshorterTMC
reactiontime)isowingtotheloosestructureofthecoatinglayer.Asthereactiontime
increased,the−OHand−C=Owouldbeenhanced,andbondingbetweentheOHandC–
Ogroupswouldreduce.Therefore,amembranewithadenselayerwouldbecreated
[51,53].
3.ImprovementofInterfacialBonding
Generally,thetubularbraidsandseparationlayersareincompatible.Thethermody‐
namicalincompatibilityofthesetwolayermaycauseanapparentchangeininterface
structurebetweenthesupportedmatrixandseparationlayer.Therefore,theinterfacial
bondingstrengthbetweenthebraidandtheseparationlayerisacrucialissueinthebraid‐
reinforcedhollowfibermembrane.Thepeelingoftwolayersduringthemembraneoper‐
ationprocessreducesitslifetimeandrestrictsitsapplication.Hence,theaffinity(compat‐
ibility)betweentwolayersplaysavitalroleinthestrengthofinterfacialbonding.The
highinterfacialbondingstrengthisfavorableinhigh‐pressurehydrauliccleaning.The
infiltrationpropertyofBHFMsisinvestigatedbythecontactanglebetweenthebraidand
polymersolution[44,45,54].
3.1.HybridBraidHollowFiberMembranes
Theselectionofmaterialforpolymerandtubularbraidaffectstheinterfacialbonding
performance.RelativetoheterogeneousBHFM(braidsandseparationlayeraremade
fromdifferentmaterials),homogeneousBHFMthatcontainedthesamematerialsinthe
Membranes2021,11,88416of31
tubularbraidandtheseparationlayerhasdesirableinterfacialbondingstrength.Thein‐
terfacialbondingofthehomogenousandheterogeneousmembranedifferedfromeach
other.Theinterfacialbondingbetweenthebraidandtheseparationlayerispoorinhet‐
erogeneousBHFMduetoincompatibility,whereastheseparationlayerisstrongly
bondedwiththebraidinhomogenousBHFM.WhentheheterogeneousBHFMsaresub‐
jectedtopressingorstretchingeffect,thedeformationratewillbedifferentbetweenthe
braidlayerandtheseparationlayer.Therefore,theinterfaceoflayerswouldbehurt
throughtheinterlaminarshearbetweenthebraidlayerandtheseparationlayer.Hence,
theinterfacialbondingoftheheterogeneousBHFMisthemainparameterrestrictingits
application[6,7,21,28,36,44].Thereisaphysicalforcebetweentubularbraidsandthepol‐
ymercastingsolutioninthepreparationprocessofBHFM.Thisphysicalforceconsistsof
adhesivecuring(whentwosurfacescombinebythephysicalorchemicalinteraction)and
mechanicalwedgingthatisrelatedtothediffusiondegreeofthepolymersolutionstothe
hybridtubularbraidandthesurfaceroughnessofthehybridtubularbraids.Poorinfiltra‐
tionbetweenthehybridtubularbraidsandthepolymersolutionsresultsindefects,and
theinterfacialbondingstrengthwouldbeconsequentlyreduced.Thusadesirableinfil‐
trationperformancecanconsiderablyimprovetheinterfacialbondingstrength.Gener‐
ally,thecontactangleisusedinordertocharacterizetheinfiltrationability.Thesmaller
contactanglebetweenthepolymersolutionsandtubularbraidrevealsthebetterthein‐
filtrationperformance[6,7].Oneofthemethodstoenhanceinterfacialbondingisutilizing
thesamematerialbetweenthecoatinglayerandthereinforcedmatrix.Fanetal.prepared
anovelbraidhollowfibermembraneconsistingofahybridbraid(containingcellulose
acetateandpolyacrylonitrile)andaseparationlayer.Theresultedmembraneprovideda
wellinterfacialbondingstateandreducedthenegativeeffectofCAfiberswellingon
membranepermeability.Fanetal.alsoinvestigatedtheeffectofbraidcompositionand
CAconcentrationonBHFMperformance.Theyresultedthatthebestratioofthefibersin
thebraidphaseis2/1(CA/PAN)byconsideringthemembranepermeabilityandinterfa‐
cialbondingstate[21].Theinfiltrationofthepolymersolutionmayreducethepurewater
permeability(PWP).ItwasreportedthatPWPofthehomogeneouslyBHFMislowerthan
heterogeneousBHFMbecauseinfiltratedpolymerscanbetightlyincorporatedinthepo‐
rousbraidandthusreducethePWP[11].
Zhouetal.[36]preparedabraidhollowfibermembranewithdesirableantifouling
propertiesandmechanicalstrengthforwastewatertreatment.TheblendingPVCwith
PVC‐co‐PEGmethylethermethacrylate)(poly(VC‐co‐PEGMA))copolymercoatedon
PETbraid.Thehighinterfacialbondingandtensilestrengthindicatedthegoodcompati‐
bilitybetweenthePET‐braidandcoatinglayer.Excellentantifoulingproperties,higher
hydrophilicity,andBSArepulsionresultedduetothesegregationofPEGMAonthemem‐
branesurface.Chenetal.[28]fabricatedthreeBHFMswithPMIAasapolymeranddif‐
ferentbraidcompositions(differentratiosofPMIA/PET).AsshowninFigure7,thecoat‐
inglayerofpurePMIAforthebraidindicatedahomogeneousstructurewithgoodcom‐
patibilityandfirmlybondingbetweenthereinforcedbraidandseparationlayer;whereas,
poorinterfacialbodingandheterogeneousseparationlayerswereobservedforbraidwith
purePET.ForthebraidcontainedbothPMIAandPET,thetightlybondedforseparation
layerwiththePMIAfibersandthePETfibersobserved;whereas,therewasthepoorin‐
terfacialbondingbetweenthePETfibers.
Membranes2021,11,88417of31
Figure7.Thecross‐sectionmorphologiesof(M1)PurePMIAforthebraid(M2)equalcomposition
ofPMIA/PETforthebraids,and(M3)PurePETforthebraids[28].
Itseemsthehybridbraidisaneffectivemethodwithhighperformance,butitishard
toapplyonalargescale.ItischallengingtofabricateBHFMconsistingofhybridbraids
(withhydrophilicpolymeric)andthesamematerialonthecoatinglayer.Therefore,itis
necessarytodevelopaneasy,effective,andlow‐costproceduretocontroltheproperties
ofthecommercialbraids[11].
3.2.AlkalinePretreatment
Alkalinepretreatmentofthebraidsurfaceisasimplemethodforincreasingandfa‐
cilitatingpolymeradhesion.Italsoleadstoincreasebraidhydrophilicity.Thismethod
providesgoodsupportforthecoatinglayerwithoutreducingthequalityofthebraid.El‐
Badawyetal.[4]investigatedtheeffectofthealkalinepretreatmentofthebraidonBHFM
morphologyandperformance.Themembraneistreatedbytwoalkalinesolutions(KOH
andNaOH).ThetreatedmembraneinKOHhadthehighestwaterflux.Theinvestigation
ofthesurfacemorphologyofthebraidsrevealedthattheexpansionofthebraidinter‐
spacesandwashingeffectcontributetomoreporosityandpermeability.
Zhouetal.[11]preparedaBHFMbycoatingablendedpolymer(amphiphiliccopol‐
ymer/PVC)solutiononamodified(alkaline‐treated)PETbraid.Themodificationbyal‐
kalineleadstoendowmorepolargroupstoPETbraidandconsequentlymorehydro‐
philicity.BasedontheresultsofZhouetal.[11],thebondingstrengthbetweenthecoating
layerandalkaline‐treatedPETbraidwasabouttwotimeshigherthanthenon‐treatedPET
braid.ThetensilestrengthofthePETbraidswasreducedafterthealkalinetreatment.The
basicPETbraidhadmoretensilestrengthrelativetotreatedPET.Thedecreasingmechan‐
icalstrengthindicatedthatthePETbraidswereweakenedbythehydrolysisofPETchains
duringthealkalinetreatment.Thehydrolysisprocessreducesthecrystallinityandthe
molecularweightofPET.Thedefectscreatedonthebraidsalsoleadtodecreasingthe
mechanicalstrength.Hence,thetreatmentconditions(alkalineconcentration,reaction
time)shouldbeoptimizedforobtainingastrongbraidmembrane.Thewaterabsorption
ratioofthePETfibersincreaseswithincreasingKOHconcentrationandtreatmenttime,
indicatingthehydrophilicityofthePETbraidsisimproved.Theincreaseinwateradsorp‐
tionisattributedtothehydrolysisofPETduringthealkalinetreatmentwhentheester
groupsexcitinginPETarehydrolyzedtohydroxylandcarboxylategroups.Longtreat‐
menttimeandhighalkalineconcentrationcausespeedupthehydrolysis,bindingmore
hydrophilicgroupsandimprovingthehydrophilicityofthebraids.Thehighestwater
adsorptionandthebesthydrophilicityareattributedtothemostporousstructureofthe
PETbraids.Therefore,thehydrophilicpolymersolutioncanquicklyinfiltrateintothe
braidandfillthebraidedchannelduringthefabricationprocess.Thenthebraidedchannel
isblockedduringthepolymersolidificationinthecoagulationbath.Thebraidwithhigher
hydrophilicityincreasestheinfiltrationofthehydrophiliccoatingsolutions,whichre‐
ducestheporosityandporesizeonthebraid.Thus,PWPwassignificantlydecreased.
However,thebraid’shydrophilicitycanbeincreasedbyhydrolysis,butthehydrolysis
processshouldbeoptimizedtoavoidPWPreduction.Theinterfacialbondingstrength
Membranes2021,11,88418of31
betweenthehydrophilicPETbraidandcoatinglayerwasmorethantheseparationlayer
andthehydrophobicbraid.Afteralkalinemodification,carboxylatesandhydroxyl
groups,asthenewlypolargroups,resultinincreasingthesurfaceenergyonthebraids
tube.Consequently,highinfiltrationleadstoincreasingthebondingstrength.
3.3.ModificationoftheBraidSurface
Anotherapproachforoptimizingtheinterfacialbondingabilityisthemodification
ofthesurfacebycoatingmethods.Liuetal.[55]modifiedtheoutersurfacesofthebraided
tubeswithsilanecouplingagentKH570andacrylateadhesivebeforefabricationofthe
fibertubereinforcedHFM.BasedonFigure8,coatingtheoutersurfaceofthefibertubes
byacrylateadhesiveandsilanecouplingageleadstofillingthegapoftheloopsandthe
groovesbetweenthefibers.Asignificantimprovementintensilestrengthwasreported
byLiuetal.intheoptimumamountofmodifiersdosages.Whenthedosageoftheacrylate
adhesiveexceededtheoptimum,theroleofvoidsblockingwasmorethantheadhesion
onthemembrane.Hence,thefluxofthemembranedecreased,andmembraneresistance
increased.Itisalsoreportedthatanincreaseinsilanecouplingagentamounthasaposi‐
tiveeffectonfiberwettabilityandporosityduetocreatingspongierporesinthemem‐
branestructure.Figure8showsthediagramofamodificationofthebraidsurfacewith
thesilanecouplingagent.Anotherfeasibleapproachwastomodifythefibertubebyphys‐
icalorchemicalmethods,suchascoatingwithmodifiersonthesurfaceofthefibertube
orintroducingchemicalgroupsthathelpincreasetheaffinityofthefibertubetothemem‐
brane[55].Figure9indicatestheeffectofmodificationofthebraidsurfaceontheinterface
ofpolymerandbraid.
Figure8.SurfacemodificationforthebraidedtubeswithsilanecouplingagentKH570[55].
Membranes2021,11,88419of31
Figure9.Schematicdiagramoftheinterface[55].
3.4.ThePresenceofAdditive
Peechmanietal.[24]reportedthattheintroductionoftheZnOnanoparticlesinPSf
dopesolutionpromotedtheinfiltrationofthedopesolution.Itisbecauseofthehydro‐
philicpropertyofZnOthatfacilitatestheinfiltrationofthecoatingsolutionintothe
braidedsupportandaccumulatesbetweenthebraidchannelsduringthepreparationpro‐
cess.Moreinfiltrationofcoatingsolutionintothebraidedsupportwillenhancetheme‐
chanicalstabilityoftheBHFMduetothetightbondingbetweentheselectivelayerwith
thebraidlayerthatpreventsthepeelingoftheselectivelayerfromthebraidedsupport.
ZnOnanoparticlesalsoinfluencedthethicknessoftheseparationlayer.Themembrane
withoutnanoparticleshadathickerseparationlayerrelativetotheothermembranesbe‐
causeofthelowerinfiltrationrateandtheunevencircularshapeofthebraidlayerduring
thespinningprocess(becauseofmechanicalstressthathandledtopullthebraidlayerout
fromthespinneret).
Membranes2021,11,88420of31
Table2.SummaryofBHFMstudies.
PolymerCoating
Solution/wt.(%)
AdditiveinCoating
Solution/wt.(%)
Braid(Threads/Fil‐
ament)Composi‐
tion
TypeofSpinning
Methods/
SpinningConditions
InvestigatedParameters
Opera‐
tional
Condi‐
tion
Impurities/Ap‐
plicationResultsComparison
withHFMRef
Hybridbraid
Polymer:CA;
10,12,14(wt.%)
Additive:PEG:20
wt.%
CA/PAN
Dry–wetspinning/
- coagulationbath:
water(25°C)
- air‐gapdistance:
10cm
- take‐upspeed:100
cm/min
- Theeffectofbraidcom‐
position
- Theeffectofpolymer
(CA)concentrationonthe
structureandperformance
Pres‐
sure:0.1
MPa
BSAsolution
Milksolution
MaxTensilestrength
(MPa):33.8forCA14
and
62.9MPaforpurePAN
inthebraid
MaxBSARejection:
CA10:90%
CA12:98%
CA14:99%
MaxPWF:300L/m2hr
for1/2(CA/PAN)
Maxburstingstrength
(MPa):0.75forpureCA
inthebraid
Minburstingstrength
(MPa):0.22forpure
PANinthebraid
NA[21]
Polymer:PVC:
12wt.%
Additive:PVP
10wt.%
PET/PAN
Dry–wetspinning
/
- coagulationbath:
water(28°C)
- air‐gapdistance:
12cm
Take‐upspeed:66
cm/min
- Theeffectofbraidcom‐
positiononthestructure
andperformance
Pres‐
sure:0.1
MPa
BSAsolution
MaxTensilestrength
(MPa):106forpurePET
MaxBSARejection:
70%for1/1:PET/PAN
‐Highertensile
strengthrela‐
tivetoHFM
[6]
Polymer:PMIA
5,8,10,15(wt.%)
Additive:PVP
PMIA/PET
Dry–wetspinning
/
- Coagulationbath:
water(25°C)
- Theeffectsofpolymer
concentration
Pres‐
sure:0.1
MPa
skimmilksolu‐
tion
MaxPWF:296.85
L/m2hrforPMIA5
MaxBSARejection:
NA[28]
Membranes2021,11,88421of31
2wt.%,PEG:8,
CaCl2:3.5,LiCl:2.5
wt.%
- Air‐gapdistance:
15cm
Take‐upspeed:50
cm/min
- Theeffectsofbraid
composition
97.9%forPMIA15
MaxTensilestrength
(MPa):179.15for
PMIA15
Maxburstingstrength
(MPa):0.98PMIA15
Polymer:PVDF:18
wt.%
Additive:PEG:3
wt.%
PVDF‐
PET
NIPS:Dry–wetspin‐
ning/
- CoagulationBath:
water(25°C)
- Air‐gapdistance:
10cm
Take‐upspeed:2RPM
- Theeffectofpretreat‐
mentstepbyalkaline
methodonperformance
Pres‐
sure:0.1
MPa
NA
MaxPWF:1388L/m2hr
formembranetreatby
KOH
MaxTensilestrength
(MPa):113formem‐
branetreatbyKOH
NA[4]
Polymer:PVC
6,8,10,12,14(wt.%)
Additive:PEG
5
Dry–wetspinning/
- Coagulationbath:
water(20°C)
- Air‐gapdistance:
8cm
Take‐upspeed:220
cm/min
Dopesolutiontempera‐
ture:70°C
- ‐Theeffectofpolymer
Concentration
- Theeffectofadditive
molecularweight
NA
MaxPWF:10.1L/m2hr
for
PVC10
MaxBSARejection:
76.12%forPVC10and
PEG6000
‐Higherrejec‐
tion
‐Higherflux
recoveryrate
[29]
Purebraid
Polymer:CA
6,8,10,12,14(wt.%)
Additive:PEG6000:6
PEG400:10
CA
Dry–wetspinning/
- Coagulationbath:
water(20°C)
- Air‐gapdistance:
10cm
Take‐upspeed:66
cm/min
Dopesolutiontempera‐
ture:70°C
- Theeffectsofpolymer
concentration
Pres‐
sure:0.1
MPa
NA
MaxTensilestrength
(MPa):14.2forCA14
Maxburstingstrength
(MPa):0.51forCA14
MaxPWF:220L/m2hr
for
CA6
MaxBSARejection:
90%forCA14
NA[37]
Membranes2021,11,88422of31
Polymer:PAN
8,10,12,14,16(wt.%)
Additive:PVP
(7wt.%)and
Tw‐80(2wt.%)
PAN
Dry–wetspinning/
- coagulationbath:
water(25°C)
- air‐gapdistance:
15cm
Take‐upspeed:20
cm/min
Dopesolutiontempera‐
ture:70°C
- Theeffectofpolymer
(PAN)concentrationin
coatingsolution
- Theeffectoftwotype
ofbraidcomposition
Pres‐
sure:0.1
MPa
BSAsolution
Tensilestrength(MPa):
86.3
MaxPWF:345L/m2hr
forPAN10
MaxBSARejection:
91%forPAN18
NA[7]
Polymer:PAN
8,10,12,14,16(wt.%)
Additive:PVP
(7wt.%)and
Tw‐80(2wt.%)
PET
Dry–wetspinning/
- coagulationbath:
water(25°C)
- air‐gapdistance:
15cm
Take‐upspeed:20
cm/min
Dopesolutiontempera‐
ture:70°C
- Theeffectofpolymer
(PAN)concentrationinthe
coatingsolution
- Theeffectoftwotypes
ofbraidcomposition
Pres‐
sure:0.1
MPa
BSAsolution
Tensilestrength(MPa):
188
MaxPWF:470L/m2hr
forPAN10
MaxBSARejection:
91%forPAN18
NA[7]
Polymer:PVC
Additive:poly(VC‐
co‐PEGMA)
PET
Dry–wetspinning
/
- coagulationbath:
water(24°C)
- Air‐gapdistance:
0.5cm
Take‐upspeed:500
cm/min
Dopesolutiontempera‐
ture:45°C
UFBHFMfor
wastewater
treatment
‐Highertensile
strength
‐Higherburst‐
ingstrength
‐Lowerthick‐
nessforthe
coatinglayer
[36]
Polymer:PSf:16
wt.%
Additive:ZnO
0,0.5,1,1.5(wt.%)
Dry–wetspinning
/
- coagulationbath:
water(25°C)
- Air‐gapdistance:
10cm
- Take‐upspeed:200
cm/min
Pres‐
sure:0.1
MPa
1000ppmBSA
solution
MaxPWF:920L/m2hr
forZnO:1.5
MaxBSARejection:
96.5%forZnO:1.5
‐Higherwater
flux
‐higherrejec‐
tion
[24]
Membranes2021,11,88423of31
Polymer:PVDF
15,20,25,30(wt.%)
Additive:PVP
20wt.%PVDF
PETDry–wetspinning/
- Effectofpolymercon‐
centrationindopesolution
- NumbersofPET
threads(n)
Pres‐
sure:0.1
MPa
Purewater
Maxtensilestrength
(MPa):11.15for
PVDF20and3PET
threads
MaxPWF:160L/m2hr
forPVDF18
Maxburstingstrength
(MPa):0.45PVDF30
‐Highertensile
strength
‐similarsepa‐
rationproper‐
ties
[46]
Polymer:PVDF13
(wt.%)
Additive:Ge
0,0.1,0.3,0.5,0.7
(wt.%)
SiO2:4,DOP:10
PET
Dry–wetspinning
/
- coagulationbath:
water(30°C)
- Air‐gapdistance:
20cm
Take‐upspeed:120
cm/min
Dopesolutiontempera‐
ture:70°C
‐Theeffectofadditive
concentration0.1MPa
keroseneand
watermixture
(1:1,
v/v)/oil/water
separation
MaxRejection:
99.7%forGe:0.5
PWF:65L/m2hrfor
GE:0.5
NA[38]
Polymer:PU
16wt.%
Additive:Ge
0.0.1,0.3,0.5(wt.%)
SA:4,NaCl:0.2
PET
Electrospinning
method/
- Positivepressureof
thespinneret:25.5kV
- Negativepressure
ofthereceivingdevice:
5.5kV
- Receivingdistance:
10cm
- Receivingdevice
speed:1500rpm
- Spinningsolution
injectionspeed:2.1mL/
h
- Spinningtempera‐
ture:25°C
‐Theeffectofadditive
concentration0.1MPa
keroseneand
watermixture
(1:1,
v/v)/oil/water
separation
MaxRejection:
99%forGe:0.3
PWF:1443L/m2hrfor
GE:0.3
NA[43]
Membranes2021,11,88424of31
- Relativehumidity:
5%
Polymer:PVDF
8,10,12,14,16(wt.%)
Additive:PVP:8
(wt.%)
Tw‐80:2(wt.%)
PAN
Dry–wetspinning/
- coagulationbath:
water(25°C)
- Air‐gapdistance:
15cm
Take‐upspeed:15
cm/min
Dopesolutiontempera‐
ture:70°C
Theeffectofpolymercon‐
centrationincoatingsolu‐
tions
Pres‐
sure:0.1
MPa
1g/L
BSA
Maxtensilestrength
(MPa):75
MaxPWF:550L/m2hr
forPVDF8
MaxBSARejection:
95%forPVDF16
NA[40]
Polymer:PVDF
6,8,10,14,18(wt.%)
Additive:PVP:7
(wt.%)
Tw‐80:3(wt.%)
PVDF
Dry–wetspinning
/
- coagulationbath:
water(20°C)
- Air‐gapdistance:
10cm
Take‐upspeed:15
cm/min
Dopesolutiontempera‐
ture:60°C
- Theeffectofpolymer
concentrationincoating
solutions
Pres‐
sure:0.1
MPa
2g/L
Eggalbumen
Maxtensilestrength
(MPa):11forPVDF10
MaxPWF:900L/m2hr
forPVDF6
MaxBSARejection:
81%forPVDF18
‐Highertensile
strength
‐HigherBSA
rejection
[45]
Polymer:CA
Additive:Ge‐ ‐
- TheeffectofGecon‐
centrationincoatingsolu‐
tions
‐ ‐
Maxtensilestrength
(MPa):30
MaxPWF:158.1L/m2hr
forGe:1%
NA[56]
Polymer:PA
PIP:2.0%w/vTMC:
0.13%v/v
Polymer:PSf:16
(wt.%)
Additive:PVP10
(wt.%)
Interfacialpolymeriza‐
tionofPIPandTMCon
UFsupportmembrane
- TheeffectofTMCreac‐
tiontime
Pres‐
sure:0.6
MPa
MgSO4
NaCl
TOC/
TFCNF
MaxPWF:5.1L/m2hr
MgSO4Rejection:65%
NaClRejection:26%
TOCremoval:65%
NA[51]
Polymer:PA
PIP:1.0%w/w
TMC:0.1,0.15,0.2%
w/v
PVDFandpolyes‐
ter
Interfacialpolymeriza‐
tionofPIPandTMCon
UFsupportmembrane
- Theeffectofmonomer
concentration
Pres‐
sure:0.1
MPa
MgSO4
NaCl/
TFCNF
MaxPWF:22L/m2hr
MaxMgSO4Rejection:
92%
NaClRejection:˂30%
NA[10]
Membranes2021,11,88425of31
PMIA:Poly(m‐phenyleneisophthalamide);PVDF:Polyvinylidenefluoride;poly(VC‐co‐PEGMA):amphiphiliccopolymerpoly(vinylchloride‐co‐poly(ethyleneglycol)
methylethermethacrylate);NIPS:non‐solvent‐inducedphaseinversion;PA:polyamide;PET:Polyethyleneterephthalate(PET);Ge:Graphene;DOP:Dioctylphthalate;
PU:polyurethane;SA:Stearicacid;BSA:bovineserumalbumin;PIP:piperazine;TMC:trimesoylchloride;PWF:purewaterflux;PVP;Polyvinylpyrrolidone;NA:not
applicable.
Polymer:PVDFFiberglassmaterial‐
- Estimationoftheten‐
silestrengthofMFandUF
hollowfiberbraidmem‐
brane
‐ ‐
Maxtensilestrength
(MPa):10formembrane
with0.355Thickness
NA[57]
Membranes2021,11,88426of31
4.OperationParameters
AnincreaseinoperatingpressureleadstotheenhancementofPWF.Thisincreaseis
slowedinhigheroperationpressurethatisclearinalowerconcentrationofpolymer.Itis
probablyduetomorecompressionoftheporousmembraneinhighpressureandmore
resistancetothecompactionforlessporousmembrane[46].Peechmanietal.[24]indi‐
catedtheBSArejectionwasapproximatelyconstant,andthefluxincreasedwhentheop‐
eratingpressureincreased.Xiaetal.[10]testedtheperformanceofTFC‐BHFMunder
pressureuntilfailureintermsofMgSO4rejectionandwaterflux.Aslightenhancingof
MgSO4rejectionandalinearincreasewasobservedforwaterfluxbytheenhancementof
pressureupto0.5MPa.Thedropinsaltrejectionandasharpincreaseinwaterfluxupto
0.5MPaindicatesmembranedelaminationortearingoftheselectivelayer.
Chenetal.[28]reportedthattheincreaseintheoperatingtemperaturefrom25°Cto
90°Cleadstoanincreaseinwaterfluxbecauseofareductioninwatersolutionviscosity.
Theyinvestigatedtheperformanceoftailoring‐PMIA‐BHFMandcommercial‐PVDF‐
BHFMatdifferenttemperatures.AccordingtoFigure10,theinksolutionrejectionwas
stableforPMIAbraidhollowfibermembranes,whereasitwasdecreaseddramaticallyfor
thePVDF‐BHFM.ThePMIAbraidhollowfibermembranesexhibitedthermalstability,
whilethePVDFmembranefacedacrucialcracking.Itisthemainreasonforthereduction
intherejectionoftheinksolution.Thepresenceofintermolecularhydrogenbondingand
largebenzeneringsinmacromolecularchainsofPMIAleadstoahighglasstransition
temperature(morethan270°C).Hence,theporestructureismaintained,anddeformation
hasnothappenedindifferentthermalconditions.ThePMIAbraidhollowfibermem‐
branesarethusintroducedforapplicationinseparationprocesseswithhightempera‐
tures.
Figure10.Theeffectoftemperatureonrejectionandfluxof(a)PMIA‐BHFMand(b)PVDF‐BHFM.
5.Applications
Hollowfibermembranesaredesirablefornumerousmembraneapplications.They
arefavoredforuseinwatertreatmentprocessesduetothedesirablepropertiesmentioned
above[9].Submergedmembranebioreactorisusuallyutilizedtoremovecommonpollu‐
tantsfrommunicipalandindustrialwastewaterbecauseofmanyadvantagessuchas
high‐qualityeffluent,lowsludgeproduction,andreducedfootprint.Themodulecanbe
preparedbytheflatsheetorhollowfibermembranes,buttheHFMshavebeenmore
widelyusedduetoeasyassemblingandhighpermeabilityperinstallationarea.However,
HFMinthesubmergedMBRisrequiredhighmechanicalpropertiesbecauseofeasilybro‐
kenduringthehigh‐pressureback‐washingandcleaningprocessoraeratedairflow
Membranes2021,11,88427of31
[37,40,58].Fanetal.[37]investigatedtheBHFMintheMBRprocess.Thetensilestrength
ofpreparedBHFMswashigherthan11MPa,whichthiscontentincreasedwiththein‐
creaseinpolymerconcentrationindopesolution.
Generally,thehollowfibermembranesarenotapplicableinhigh‐pressureapplica‐
tionssuchasNFandROprocessesbecauseoftheirpoormechanicalstrength.Whereas
theyaregoodcandidatesforwastewatertreatment,removalofheavymetals,anddrink‐
ingwaterpurification[10,15,51].Thin‐filmcomposite(TFC)membranesareexcellentcan‐
didatesforROandNFprocessesinwaterandwastewatertreatmentapplicationsdueto
theultrathinselectivelayer.TheTFCdesignpossessesdesiredperformanceintermsof
saltrejectionandpermeabilitywhenunitedwithasymmetricmembranes.Thecross‐
linkedaromaticpolyamideasaselectivelayerontheultrafiltrationmembraneporousor
othersupportingsubstratesfabricatedbyinterfacialpolymerizationofpropermonomer
(e.g.,trimesoylchloride(TMC))isthemostsuccessfulandfamouscommercialproductin
thelastdecades[10,50,59].Asmentioned,TFCmembranesconsistofasupportlayerand
selectivelayer.Theselectivelayerthattypicallycross‐linkedpolyamideisathin,dense,
andpoormechanicalfilmwithhighselectivity.Thesecondlayerisaporousfilmthat
playstheroleofthesubstratewithhighmechanicalstrengthunderpressure.Thislayer
generallyisformedfrompolyethersulfoneandpolysulfone.Figure11illustratestheshell
andlumensideofHFM.Generally,itisdifficulttoapplyathinfilmontheshellorlumen
sideoftheHFMduringfibermanufacturing.TheHFMsdesignedforliquidfiltrationhave
largelumensduetoreducingresistanceinmasstransferandpressuredropliquidstream.
Inhigh‐pressureapplications,thewallsofHFMsmustbethicker,butitisnotdesirable
forliquidflowapplications.ItisreportedseveralstudiesonthefabricationofHFMwith
high‐pressuretoleranceandimprovementofmechanicalstability.Thesestudiespropose
usingapolymer/additivewithintrinsichighmechanicalstrength,optimizationofspin‐
ningparameters,andbraidreinforcedcomposition[10,60].Xiaetal.[10]fabricatedaTFC‐
HFMthatusesabraid‐reinforcedultrafiltration‐HFMsasasubstrate,consistingofaPVDF
coatinglayerandpolyesterbraid.Theselectivelayerisformedusinginterfacialpolymer‐
izationofTMCandpiperazine(PIP).Thepresenceofthereinforcedsupportdevoted
high‐pressureenduranceproprietiestotheHFM.Thepreparedmembranescouldtolerate
pressureupto0.5MPawhilepossessinghighselectivityfordivalent/monovalentions.
Turkenetal.[51]fabricatedreinforcedTFC‐HFNFbasedonPSfultrafiltrationmem‐
branesandpolyamidelayerpreparedfromPPandTMCmonomers.Themembraneswere
investigatedinsolutionswithdifferentorganicmatterandsalts.Theirresultsevidenced
thepreparedmembranesareagoodcandidateforwater‐treatmentapplications
Figure11.TheillustrationofshellandlumensideofanHFM[61].
AnotherapplicationofBHFMsistheoil/waterseparationprocess.Oilywastewater
isproducedbydifferentindustriessuchasmetalfinishingindustries,leather,food,pet‐
rochemical,oilexploration,refining,andtransportationofoilproducts.Thistypeof
Membranes2021,11,88428of31
wastewaterisaseverethreattohumanhealthandtheenvironment.Membranetechnol‐
ogyisaproperoptionforoilywastewaterstreatmentowingtoadvantagessuchaslow
costs,nosecondarypollution,highenergyefficiency,sustainability,andnoadditives.
Twoparametersareessentialfortheoil/waterseparationprocess:theselectivewettability
foroilorwater(lipophilicity/hydrophobicity)thatprovidetherequireddrivingforceand
theconnectedporeswithasuitableporesizeforfiltration.Bothhydrophobicandhydro‐
philicmembranescouldbeutilizedfortheseparationofoil/water.Hydrophilicmem‐
branesincreasethewaterpermeationrelativetooilpermeationleadingtohigherwater
fluxandgoodantifoulingproperties.Nevertheless,thehydrophilicmembranesmustpro‐
videalargevolumeofwaterpermeatefluxesinseparationsofoil/water.Theyrequired
highenergyconsumptionandlargemembraneareas.Generally,thepresentpollutantsin
oilywastewateraremainlyduetotheoilphase,buttheircontentsarerelativelylow.
Therefore,hydrophobicmembranesarebettercandidatesforoilywastewatertreatment
basedonworkload[38,43].Haoetal.[38]prepared(PET‐)braid‐reinforcedPVDF/gra‐
phenehollowfibermembranes.PVDF‐BHFMshowsappropriatehydrophobicproperties
foroil/waterseparationandgoodmechanicalstrength.Graphenewasalsousedtoen‐
hancethehydrophobicityofthemembrane.Theirresultsshowedthatthepreparedhy‐
drophobicBHFMsultimatelyrejectedwaterduringtheseparationprocess.
6.Conclusions
Hollowfibermembranes(HFMs)areagoodcandidateforthemembraneseparation
processduetodesirablepropertiessuchashighpermeabilityandsurfacearea,goodfil‐
trationefficiency,smallfootprint,etc.However,theyareoftenpossibletobreakduring
thehigh‐pressurecleaningandaerationprocess.Tubularbraidsasupportedisproposed
toimprovethemechanicalstrengthofHFMsduetohightensilestrength.Thepeelingof
thesurfacelayerfromthetubularbraidisthedrawbackoftheBHFMduetothermody‐
namicincompatibility.Dependingonthetypeofapplication,thekindofpolymer/addi‐
tiveandtheircontentaretheessentialparametersthataffecttheperformanceofBHFMs.
PAN,PVC,CA,PSf,andPVDFarethecommonpolymersusedinBHFMpreparation.The
interfacialbondingstrengthbetweenthebraidandtheseparationlayerisanessential
issueinBHFMs.Becausetheseparationoftwolayersreducesitslifetimeandlimitsits
application;hence,theaffinitybetweenthetwolayerswillbeimproved.Theinterfacial
bondingstrengthbetweenthebraidandtheseparationlayerisanessentialissuein
BHFMs.Hence,theaffinitybetweenthetwolayerswillbeimprovedbyhybridbraids,
alkalinepretreatment,andtheuseofadditives.Recently,theBHFMshavebeenusedin
ROandNFapplications.Althoughitisrequiredacomprehensiveinvestigationthatopti‐
mizesthemembraneperformanceintermsofflux,mechanicalproperties,rejection,and
fouling;itisexpectedthattheapplicationsofthesetypesofthemembranewillbeen‐
hancedindifferentaspectsandthegapbetweenstudiesandapplyinlargescaleswould
bereduced.
AuthorContributions:Conceptualization,A.N.,H.K.,E.S.,S.M.M.andH.M.,Datacuration,A.N.,
Formalanalysis,A.N.,H.K.,E.S.,S.M.M.andH.M.,Investigation,A.N.,H.K.,E.S.,S.M.M.andH.M.,
Methodology,A.N.,H.K.,E.S.,S.M.M.andH.M.,Visualization,A.N.,H.K.,E.S.,S.M.M.andH.M.,
Validation,A.N.,H.K.,E.S.,S.M.M.andH.M.,Writing,A.N.,H.K.,E.S.,S.M.M.andH.M.,Original
draft,A.N.,Authorship,A.N,H.K.,Projectadministration,H.K.,Supervision,H.K.,review&edit‐
ing,H.K.,Resources,E.S.,S.M.M.andH.M.,Fundingacquisition,H.M.Allauthorshavereadand
agreedtothepublishedversionofthemanuscript.
InstitutionalReviewBoardStatement:Notapplicable.
Funding:Thisresearchreceivednoexternalfunding.
InformedConsentStatement:Notapplicable.
DataAvailabilityStatement:Notapplicable.
ConflictsofInterest:Theauthorsdeclarenoconflictofinterest
Membranes2021,11,88429of31
Abbreviation
HFM:Hollowfibermembrane
BHFM:BraidHollowfibermembrane
PMIA:Poly(m‐phenyleneisophthalamide)
PVDF:Polyvinylidenefluoride
Poly(VC‐coPEGMA):Poly(vinylchloride‐co‐poly(ethyleneglycol)methylethermethacry‐
late)
NIPS:Non‐solvent‐inducedphaseinversion
PA:Polyamide
PET:Polyethyleneterephthalate
Ge:Graphene
DOP:Dioctylphthalate
PU:Polyurethane
SA:Stearicacid
BSA:Bovineserumalbumin
PIP:Piperazine
TMC:Trimesoylchloride
PWF:Purewaterflux
References
1. Al‐Maas,M.;Hussain,A.;Matar,J.M.;Ponnamma,D.;Hassan,M.K.;Al‐Maadeed,M.A.A.;Alamgir,K.;Adham,S.Validation
andapplicationofamembranefiltrationevaluationprotocolforoil‐waterseparation.J.WaterProcess.Eng.2021,43,102185.
2. Han,R.;Ma,X.;Xie,Y.;Teng,D.;Zhang,S.Preparationofanew2DMXene/PEScompositemembranewithexcellenthydro‐
philicityandhighflux.RSCAdv.2017,7,56204–56210.
3. Li,Q.;Omar,A.;Cha‐Umpong,W.;Liu,Q.;Li,X.;Wen,J.;Wang,Y.;Razmjou,A.;Guan,J.;Taylor,R.A.Thepotentialofhollow
fibervacuummulti‐effectmembranedistillationforbrinetreatment.Appl.Energy2020,276,115437.
4. El‐badawy,T.;Othman,M.H.D.;Adam,M.R.;Ismail,A.;Rahman,M.A.;Jaafar,J.;Usman,J.;Mamah,S.C.;Raji,Y.O.Theinflu‐
enceofpretreatmentsteponhollowbraidedPETfabricasapotentialmembranesubstrate.Mater.TodayProc.2021,46,1990–
1997.
5. Kim,I.;Choi,D.‐C.;Lee,J.;Chae,H.‐R.;Jang,J.H.;Lee,C.‐H.;Park,P.‐K.;Won,Y.‐J.Preparationandapplicationofpatterned
hollow‐fibermembranestomembranebioreactorforwastewatertreatment.J.Membr.Sci.2015,490,190–196.
6. Liu,H.;Wang,S.;Mao,J.;Xiao,C.;Huang,Q.Preparationandperformanceofbraid‐reinforcedpoly(vinylchloride)hollow
fibermembranes.J.Appl.Polym.Sci.2017,134,45068.
7. Quan,Q.;Xiao,C.;Liu,H.;Huang,Q.;Zhao,W.;Hu,X.;Huan,G.Preparationandcharacterizationofbraidedtubereinforced
polyacrylonitrilehollowfibermembranes.J.Appl.Polym.Sci.2015,132.https://doi.org/10.1002/app.41795.
8. Wan,C.F.;Yang,T.;Lipscomb,G.G.;Stookey,D.J.;Chung,T.‐S.Chapter11‐Designandfabricationofhollowfibermembrane
modules.HollowFiberMembr.2021,225–252.https://doi.org/10.1016/B978‐0‐12‐821876‐1.00007‐X.
9. Xia,L.;McCutcheon,J.Braided‐ReinforcedThinFilmComposite(TFC)NanofiltrationHollowFiberMembranes.InProceed‐
ingsofthe2017AIChEAnnualMeeting,Minneapolis,MN,USA,1November2017.
10. Xia,L.;Ren,J.;McCutcheon,J.R.Braid‐reinforcedthinfilmcompositehollowfibernanofiltrationmembranes.J.Membr.Sci.
2019,585,109–114.
11. Zhou,Z.;Fang,L.F.;Wang,S.Y.;Matsuyama,H.Improvingbondingstrengthbetweenahydrophiliccoatinglayerandpoly
(ethyleneterephthalate)braidforpreparingmechanicallystablebraid‐reinforcedhollowfibermembranes.J.Appl.Polym.Sci.
2018,135,46104.
12. Jeon,S.;Karkhanechi,H.;Fang,L.‐F.;Cheng,L.;Ono,T.;Nakamura,R.;Matsuyama,H.Novelpreparationandfundamental
characterizationofpolyamide6self‐supportinghollowfibermembranesviathermallyinducedphaseseparation(TIPS).J.
Membr.Sci.2018,546,1–14.
13. Matsuyama,H.;Karkhanechi,H.;Rajabzadeh,S.;.Polymericmembranefabricationviathermallyinducedphaseseparation
(TIPS)method;Elsevier:Amsterdam,TheNetherlands,2021;Chapter3.
14. Wang,K.;Abdala,A.;Hilal,N.;Khraisheh,M.Mechanicalcharacterizationofmembranes.InMembraneCharacterization;Else‐
vier:Amsterdam,TheNetherlands,2017;pp.259–306.
15. Hosseini,S.S.;Nazif,A.;Shahmirzadi,M.A.A.;Ortiz,I.;Fabrication,tuningandoptimizationofpoly(acrilonitryle)nanofiltra‐
tionmembranesforeffectivenickelandchromiumremovalfromelectroplatingwastewater.Sep.Purif.Technol.2017,187,46–
59.
16. Hou,D.;Fan,H.;Jiang,Q.;Wang,J.;Zhang,X.PreparationandcharacterizationofPVDFflat‐sheetmembranesfordirectcontact
membranedistillation.Sep.Purif.Technol.2014,135,211–222.
17. Hou,D.;Dai,G.;Fan,H.;Wang,J.;Zhao,C.;Huang,H.Effectsofcalciumcarbonatenano‐particlesonthepropertiesof
PVDF/nonwovenfabricflat‐sheetcompositemembranesfordirectcontactmembranedistillation.Desalin.2014,347,25–33.
Membranes2021,11,88430of31
18. Wei,J.;Qiu,C.;Tang,C.Y.;Wang,R.;Fane,A.G.Synthesisandcharacterizationofflat‐sheetthinfilmcompositeforwardosmo‐
sismembranes.J.Membr.Sci.2011.372,292–302.
19. Huo,R.;Gu,Z.;Zuo,K.;Zhao,G.PreparationandpropertiesofPVDF‐fabriccompositemembraneformembranedistillation.
Desalination2009,249,910–913.
20. Dabiryan,H.;Johari,M.;Bakhtiyari,S.;Eskandari,E.Analysisofthetensilebehavioroftubularbraidsusingenergymethod,
PartII:Experimentalstudy.J.Text.Inst.2017,108,1899–1904.
21. Fan,Z.;Xiao,C.;Liu,H.;Huang,Q.;Zhao,J.Structuredesignandperformancestudyonbraid‐reinforcedcelluloseacetate
hollowfibermembranes.J.Membr.Sci.2015,486,248–256.
22. Karkhanechi,H.;Rajabzadeh,S.;DiNicolò,E.;Usuda,H.;Shaikh,A.R.;Matsuyama,H.Preparationandcharacterizationof
ECTFEhollowfibermembranesviathermallyinducedphaseseparation(TIPS).Polymer2016,97,515–524.
23. Mahendran,M.;Goodboy,K.P.;Fabbricino,L.HollowFiberMembraneandBraidedTubularSupportTherefor.U.S.Patent
6,354,444B1,11March2002.
24. Peechmani,P.;Othman,M.H.D.;Kamaludin,R.;Puteh,M.H.;Jaafar,J.;Rahman,M.A.;Ismail,A.F.;Kadir,S.H.S.A.;Illias,R.M.;
Gallagher,J.HighFluxPolysulfoneBraidedHollowFiberMembraneforWastewaterTreatmentRoleofZincOxideasHydro‐
philicEnhancer.J.Environ.Chem.Eng.2021,9,105873.
25. Cooper,W.W.;Shea,E.M.ProcessforCastingIntegrallySupportedTubularMembranes.U.S.Patent3,676,193,11July1972.
26. Mailvaganam,M.;Fabbricino,L.;Rodrigues,C.F.;Donnelly,A.R.HollowFiberSemipermeableMembraneofTubularBraid.
U.S.Patent5,472,607,5December1995.
27. Teoh,M.M.;Bonyadi,S.;Chung,T.‐S.Investigationofdifferenthollowfibermoduledesignsforfluxenhancementinthemem‐
branedistillationprocess.J.Membr.Sci.2008,311,371–379.
28. Chen,M.;Xiao,C.;Wang,C.;Liu,H.Studyonthestructuraldesignandperformanceofnovelbraid‐reinforcedandthermosta‐
blepoly(m‐phenyleneisophthalamide)hollowfibermembranes.RSCAdv.2017,7,20327–20335.
29. Liu,H.;Xiao,C.;Huang,Q.;Hu,X.Structuredesignandperformancestudyonhomogeneous‐reinforcedpolyvinylchloride
hollowfibermembranes.Desalination2013,331,35–45.
30. Song,L.;Huang,Q.;Huang,Y.;Bi,R.;Xiao,C.Anelectro‐thermalbraid‐reinforcedPVDFhollowfibermembraneforvacuum
membranedistillation.J.Membr.Sci.2019,591,117359.
31. Aslan,T.;Arslan,S.;Eyvaz,M.;Güçlü,S.;Yüksel,E.;Koyuncu,I.Anovelnanofibermicrofiltrationmembrane:Fabricationand
characterizationoftubularelectrospunnanofiber(TuEN)membrane.J.Membr.Sci.2016,520,616–629.
32. Frenot,A.;Chronakis,I.S.Polymernanofibersassembledbyelectrospinning.Curr.Opin.ColloidInterfaceSci.2003,8,64–75.
33. Moattari,R.M.;Mohammadi,T.;Rajabzadeh,S.;Dabiryan,H.;Matsuyama,H.Reinforcedhollowfibermembranes:Acompre‐
hensivereview.J.TaiwanInst.Chem.Eng.2021,122,284–310.
34. Turken,T.;Sengur‐Tasdemir,R.;Ates‐Genceli,E.;Tarabara,V.V.;Koyuncu,I.Progressonreinforcedbraidedhollowfiber
membranesinseparationtechnologies:Areview.J.WaterProcess.Eng.2019,32,100938.
35. Abba,M.U.;Man,H.C.;Azis,R.S.;Idris,A.I.;Hamzah,M.H.;Yunos,K.F.;Katibi,K.K.NovelPVDF‐PVPHollowFiberMem‐
braneAugmentedwithTiO2Nanoparticles:Preparation,CharacterizationandApplicationforCopperRemovalfromLeachate.
Nanomaterials2021,11,399.
36. Zhou,Z.;Rajabzadeh,S.;Fang,L.;Miyoshi,T.;Kakihana,Y.;Matsuyama,H.Preparationofrobustbraid‐reinforcedpoly(vinyl
chloride)ultrafiltrationhollowfibermembranewithantifoulingsurfaceandapplicationtofiltrationofactivatedsludgesolu‐
tion.Mater.Sci.Eng.C2017,77,662–671.
37. Fan,Z.;Xiao,C.;Liu,H.;Huang,Q.Preparationandperformanceofhomogeneousbraidreinforcedcelluloseacetatehollow
fibermembranes.Cellulose2015,22,695–707.
38. Hao,J.;Xiao,C.;Zhang,T.;Zhao,J.;Fan,Z.;Chen,L.PreparationandperformanceofPET‐braid‐reinforcedpoly(vinylidene
fluoride)/graphenehollow‐fibermembranes.Ind.Eng.Chem.Res.2016,55,2174–2182.
39. Matsuyama,H.;Rajabzadeh,S.;Karkhanechi,H.;Jeon,S.1.7PVDFHollowFibersMembranes.InComprehensiveMembrane
ScienceandEngineering;Elsevier:Amsterdam,TheNetherlands,2017;pp.137–189.
40. Quan,Q.;Xiao,C.F.;Liu,H.L.;Zhao,W.;Hu,X.Y.;Huan,G.L.Preparationandpropertiesoftwo‐dimensionalbraidheteroge‐
neous‐reinforcedpolyvinylidenefluoridehollowfibermembrane.InAdvancedMaterialsResearch;TransTechPublicationsLtd.:
Freinbach,Switzerland,2014.
41. Rajabzadeh,S.;Ogawa,D.;Ohmukai,Y.;Zhou,Z.;Ishigami,T.;Matsuyama,H.PreparationofaPVDFhollowfiberblend
membraneviathermallyinducedphaseseparation(TIPS)methodusingnewsynthesizedzwitterioniccopolymer.Desalin.Wa‐
terTreat2015,54,2911–2919.
42. Karkhanechi,H.;Vaselbehagh,M.;Jeon,S.;Shaikh,A.R.;Wang,D.‐M.;Matsuyama,H.Preparationandcharacterizationof
polyvinylidenedifluoride‐co‐chlorotrifluoroethylenehollowfibermembraneswithhighalkalineresistance.Polymer2018,145,
310–323.
43. Wu,Y.‐J.;Xiao,C.‐F.;Zhao,J.PreparationofanelectrospuntubularPU/GEnanofibermembraneforhighfluxoil/watersepa‐
ration.RSCAdv.2019,9,33722–33732.
44. Liu,H.;Xiao,C.;Huang,Q.;Hu,X.;Shu,W.Preparationandinterfacestructurestudyondual‐layerpolyvinylchloridematrix
reinforcedhollowfibermembranes.J.Membr.Sci.2014,472,210–221.
45. Zhang,X.;Xiao,C.;Hu,X.;Bai,Q.Preparationandpropertiesofhomogeneous‐reinforcedpolyvinylidenefluoridehollowfiber
membrane.Appl.Surf.Sci.2013,264,801–810.
Membranes2021,11,88431of31
46. Liu,J.;Li,P.;Li,Y.;Xie,L.;Wang,S.;Wang,Z.PreparationofPETthreadsreinforcedPVDFhollowfibermembrane.Desalination
2009,249,453–457.
47. Lan,S.;Lei,W.;Xudong,W.;Chen,L.;Song,H.;Mingjiao,Y.HydrophilicmodificationandpropertiesofTiO2/PVDFwoven
tubalhollowfibercompositemembrane.Chin.J.Environ.Eng.2016,10,4796–4802.
48. Lee,M.S.;Lee,K.J.;Shin,Y.‐C.Braid‐ReinforcedCompositeHollowFiberMembrane.U.S.Patent7,909,177,22March2011.
49. Lee,M.S.;Lee,K.J.;Shin,Y.‐C.Braid‐ReinforcedCompositeHollowFiberMembrane.U.S.Patent8,147,938,3April2012.
50. Lau,W.;Ismail,A.;Misdan,N.;Kassim,M.Arecentprogressinthinfilmcompositemembrane:Areview.Desalination2012,
287,190–199.
51. Turken,T.;Sengur‐Tasdemir,R.;Sayinli,B.;Urper‐Bayram,G.M.;Ates‐Genceli,E.;Tarabara,V.V.;Koyuncu,I.Reinforcedthin‐
filmcompositenanofiltrationmembranes:Fabrication,characterization,andperformancetesting.J.Appl.Polym.Sci.2019,136,
48001.
52. Zhang,H.;Zheng,J.;Zhao,Z.;Han,C.C.RoleofwettabilityininterfacialpolymerizationbasedonPVDFelectrospunnano‐
fibrousscaffolds.J.Membr.Sci.2013,442,124–130.
53. Ooi,B.;Sum,J.;Lai,S.Investigationonmembranemorphologicalandchemicalpropertieschangesatdifferentreactiontimes
anditseffectondyeremoval.Desalin.WaterTreat.2012,45,250–255.
54. Huang,Y.;Xiao,C.;Huang,Q.;Liu,H.;Zhao,J.Progressonpolymerichollowfibermembranepreparationtechniquefromthe
perspectiveofgreenandsustainabledevelopment.Chem.Eng.J.2021,403,126295.
55. Liu,L.;Shen,H.;Li,T.;Han,Y.Interfacetreatmentandperformancestudyonfibertubereinforcedpolyvinylidenefluoride
hollowfibermembranes.J.Text.Inst.2020,111,1054–1063.
56. Fan,Z.;Xiao,C.;Huang,Q.;Tang,B.Modificationofbraid‐reinforcedcelluloseacetatehollowfibermembranebydopinggra‐
pheneoxide.Desalin.WaterTreat.2017,68,345–352.
57. Park,M.J.;Kim,H.Indirectmeasurementoftensilestrengthofhollowfiberbraidmembranes.Desalination2008,234,107–115.
58. Corpuz,M.V.A.;Borea,L.;Senatore,V.;Castrogiovanni,F.;Buonerba,A.;Oliva,G.;Ballesteros,F.,Jr.;Zarra,T.;Belgiorno,V.;
Choo,K.‐H.Wastewatertreatmentandfoulingcontrolinanelectroalgae‐activatedsludgemembranebioreactor.Sci.Total
Environ.2021,786,147475.
59. Li,Q.‐M.;Ma,H.‐Y.;Hu,Y.‐N.;Guo,Y.‐F.;Zhu,L.‐J.;Zeng,Z.‐X.;Wang,G.Polyamidethin‐filmcompositemembraneonpol‐
yethyleneporousmembrane:Fabrication,characterizationandapplicationinwatertreatment.Mater.Lett.2021,287,129270.
60. Davenport,D.M.;Ritt,C.L.;Verbeke,R.;Dickmann,M.;Egger,W.;Vankelecom,I.F.;Elimelech,M.Thinfilmcompositemem‐
branecompactioninhigh‐pressurereverseosmosis.J.Membr.Sci.2020,610,118268.
61. Ecker,P.;Pekovits,M.;Yorov,T.;Haddadi,B.;Lukitsch,B.;Elenkov,M.;Janeczek,C.;Jordan,C.;Gfoehler,M.;Harasek,M.
MicrostructuredHollowFiberMembranes:PotentialFiberShapesforExtracorporealMembraneOxygenators.Membranes2021,
11,374.