CN1027275C - Fibre reinforced polymeric shaped articles - Google Patents
Fibre reinforced polymeric shaped articles Download PDFInfo
- Publication number
- CN1027275C CN1027275C CN 88103280 CN88103280A CN1027275C CN 1027275 C CN1027275 C CN 1027275C CN 88103280 CN88103280 CN 88103280 CN 88103280 A CN88103280 A CN 88103280A CN 1027275 C CN1027275 C CN 1027275C
- Authority
- CN
- China
- Prior art keywords
- fiber
- formed body
- weight polyethylene
- silane
- molecular
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Expired - Fee Related
Links
Images
Landscapes
- Reinforced Plastic Materials (AREA)
Abstract
Disclosed is a fiber-reinforced polymer molded body which comprises a matrix of a polymer having a processing temperature lower than 220 DEG C and at least one reinforcing layer of a molecularly oriented and silane-crosslinked ultra-high-molecular-weight polyethylene fiber, which is laminated with or embedded in the matrix, wherein the reinforcing layer substantially retains the orientation crystal structure of the ultra-high-molecular-weight polyethylene fiber.
Description
The present invention relates to fibre reinforced polymeric shaped articles and preparation method thereof, more particularly, relate to by the matrix of polymkeric substance with lamination on the said matrix and even the molecular orientation of burying underground and with constitute and the fibre reinforced polymeric shaped articles that also has good electric property that have mechanical properties such as good snappiness rate and high strength of enhancement layer of the superhigh molecular weight polyethylene fibers of crosslinked with silicane.The invention still further relates to its making method.
Open in the clear 58-171951 communique the spy, disclosed already by the reticulattion of the polyethylene fibre of ultra-high molecular weight or polypropylene fibre and have the polyethylene crystallizing range or the fusing point in crystalling propylene interval or sticky point than the fusing point of the polyethylene fibre composite structure that constitutes of the matrix formed of low 3 ℃ polymkeric substance at least, also disclose this mixture and had the observed strength also higher than theoretical estimated value, the reason that the intensity of this mixture improves is based on certain good effect, the crystallinity loss of the fiber that produces when promptly being enough to compensate moulding.
The extension fiber of ultrahigh molecular weight polyethylene(UHMWPE) has high spring rate and high tensile strength, but still has the original shortcoming of polyethylene, i.e. poor heat resistance.
In general, by poly molecular orientation or by poly crosslinked, can improve the polyolefine thermotolerance, this point itself is known.And prior art has its oneself gauge in stable on heating raising, and after all, poly fusing point is limited in the lower temperature range, and promptly 110 and even 140 ℃, this point is inevitable basically.Known to the inventor, when poly formed body, almost all melts, and loses its intensity after 10 minutes in exposure under 180 ℃ of temperature.
Like this, what make polyolein fiber and the polymkeric substance also higher than its melting point temperature carries out compoundly substantially, and in this composite structure, the fibre reinforced polymeric shaped articles that polyolein fiber can exist under original oriented crystalline state is not so far as yet by known to the people.
Therefore, the object of the present invention is to provide a kind of composite structure of enhancement layer of the polyolein fiber that has the matrix of polymkeric substance and lamination thereon and even bury underground, polyolein fiber exists with original oriented crystalline state in this composite structure, and the result makes its fibre reinforced polymeric shaped articles with suitable snappiness rate and physical strength and preparation method thereof.
The making method of fibre reinforced polymeric shaped articles provided by the invention, it is characterized in that being made of at least one deck enhancement layer of the matrix of the polymkeric substance below 220 ℃ with lamination on said matrix and even molecular orientation of burying underground and crosslinked with silicane high molecular weight polyethylene fiber processing temperature, said enhancement layer keeps the oriented crystalline structure of high molecular weight polyethylene fiber in fact.
In addition, the making method of fibre reinforced polymeric shaped articles provided by the invention, it is characterized in that making molecular orientation and silane-crosslinked ultra-high-molecular-weight polyethylene long filament or the tNonwovens that constitutes by long filament, weave cotton cloth or compile cloth, with the configuration of face direction and the state that limits its end down with processing temperature at the polymer scale integrator below 220 ℃.
In this manual, the processing temperature of so-called polymkeric substance is to thermoplastic resin, be meant its fusing point and even softening temperature, to thermosetting resin, be meant its stiffening temperature, and to rubber, be meant its curing temperature, the fusing point and even the softening temperature of so-called thermoplastic resin to having fusing point, then only refer to fusing point, and, then be meant softening temperature to not having fusing point.
The simple declaration of accompanying drawing:
Figure 1 shows that the endothermic curve when heating up for the first time in the differential scanning calorimetry of under the restricted condition of adjusted crosslinked with silicane extension superhigh molecular weight polyethylene fibers, measuring with the method for embodiment 1;
Figure 2 shows that forming thickness with the used ultrahigh molecular weight polyethylene(UHMWPE) powder of embodiment 1 down at 200 ℃ is endothermic curve when heating up for the first time of 100 μ compacting sheet material;
Figure 3 shows that the endothermic curve when heat up the first time of extending superhigh molecular weight polyethylene fibers with the adjusted not grafting of comparative example 1;
Figure 4 shows that the paraffin that does not extend silk with embodiment 1 silane grafted uses hexane extraction at normal temperatures, it is soaked contain dibutyl tin laurate, and then the endothermic curve when heating up with the first time of the crosslinked sample of the method for embodiment 1;
The crosslinked with silicane that Figure 5 shows that Fig. 1 extends the 2nd time of the superhigh molecular weight polyethylene fibers endothermic curve of (test for the second time) when heating up.
Fig. 6 and the synoptic diagram (different) that Figure 7 shows that the fiber-reinforced resin formed body of moulding with the lamination number of embodiment;
Figure 8 shows that the graphic representation with the creep property of embodiment 1 and comparative example 1 adjusted extension orientation superhigh molecular weight polyethylene fibers, this is under 30% load with the crushing load measured under the room temperature, the result who measures under 70 ℃ the atmosphere.
Figure 9 shows that adjust with embodiment 1, crosslinked with silicane extend superhigh molecular weight polyethylene fibers and with the adhesive test of comparative example 1 adjusted orientation superhigh molecular weight polyethylene fibers in the relation of embedment length and drawing force.
The present invention is based on following new discovery: if make the molecularly oriented crosslinked with silicane fiber of ultra-high molecular weight polyethylene be combined into composite construction at the polymer below 220 ℃ with processing temperature under this processing temperature under the restrictive condition, perhaps after being combined into one, vulcanize or the processing such as sclerosis, then in the composite construction that forms, keeping in fact the oriented crystalline structure of above-mentioned fiber.
Fortifying fibre used in the present invention is formed by the material that silanes is grafted on the ultra-high molecular weight polyethylene, and makes this formation carry out crosslinked with silicane after extending to make. This extension cross moulding body has new characteristic, and namely under restrictive condition, the original fusing point of fusing point and raw material ultra-high molecular weight polyethylene of polymer chain that consists of its at least a portion is compared and increased significantly. So-called restrictive condition refers to not make fiber to be in very tense situation, but can prevent that also it from freely becoming Shape, the condition that is fixed such as the end or twisted in condition on other objects such as framework.
That is, the molecularly oriented crosslinkable silane of the ultra-high molecular weight polyethylene that the present invention uses is conjuncted, when generally under restriction state, measuring with differential scanning calorimetry, when at least high 10 ℃ temperature of the original crystalline melting temperature (Tm) of the ultra-high molecular weight polyethylene of obtaining than the main fusing peak value when heating up for the second time, at least two watery fusion peak values (Tp) being arranged, has such characteristic, namely based on this watery fusion peak value (Tp) the fusing heat be approximately the running down heat be approximately more than 5% of running down heat more than 50% and based on total fusing heat of the high temperature side fusing peak value (Tp1) of temperature range Tm+35 ℃～Tm+120 ℃.
The fusing point of polymer is fixed with the fusing of the crystallization in the polymer, generally is as the temperature of endothermic peak in the watery fusion of measuring with differential scanning calorimetry and measured. This endothermic peak temperature is fixed for the kind of the polymer of regulation, it hardly can be because of its post processing, for example extend processing and crosslinking Treatment and change, even if change, for as the maximum situation of change by the extension heat treatment that people were familiar with, also only the highlyest move about 15 ℃ to high temperature side.
These above-mentioned results show that for the independent extension and the crosslinked with silicane thing of ultrahigh molecular weight polyethylene(UHMWPE), the endothermic peak in the watery fusion is almost identical with untreated ultrahigh molecular weight polyethylene(UHMWPE), is about 135 ℃.And to the crosslinked with silicane thing, maximum value area (fusing heat) is compared with untreated, is to have reduced.The extension cross filament that the present invention is used in contrast stay little peak value on the position of the fusing peak temperature of untreated ultrahigh molecular weight polyethylene(UHMWPE), and big peak value moves on to quite high high temperature side.
Figure 5 shows that the endothermic curve when sample with Fig. 1 offers test for the second time (after the mensuration of carrying out Fig. 1, secondary intensification is measured).Result by Fig. 5 shows that under situation about heating up again, the main peak value of the watery fusion almost temperature of fusion with untreated ultrahigh molecular weight polyethylene(UHMWPE) is identical.When the mensuration of Fig. 5 because the molecular orientation in the sample almost disappears, so when being illustrated in the sample of Fig. 1 to the high temperature side of endothermic peak move with fiber in molecular orientation confidential relation is arranged.
In the orientation cross filament that the present invention uses, crystalline melting temperature is also not fully aware of to the reason that high temperature side moves, but the inventor estimates that its reason is as follows.That is to say that if silane grafting ultrahigh molecular weight polyethylene(UHMWPE) is offered the extension operation, then silane grafting part becomes the amorphousness part selectively, and partly generates the oriented crystalline part by this amorphousness.Secondly, if make this extension fiber crosslinked in the presence of silicon alcohol condensation catalyst, then become in the amorphousness part and form crosslinking structure selectively, the two ends of oriented crystalline part become with crosslinked with silicane fixed structure.For common extension fiber, watery fusion is that the amorphousness from oriented crystalline part two ends partly begins to carry out, and the present invention in contrast, the extension cross filament that the present invention uses, owing to make the amorphousness at oriented crystalline part two ends partial cross-linked selectively, polymer chain is difficult to activity, so the temperature of fusion of oriented crystalline part raises.
The molecular orientation crosslinked with silicane fiber of the ultrahigh molecular weight polyethylene(UHMWPE) that the present invention uses, even under than the also high temperature of said poly original fusing point, its fibre shape is with saying, the oriented crystalline form also can be kept, therefore under restrictive condition, make this fiber lamination and even be embedded on the various polymkeric substance, just can obtain at all good fibre reinforced polymeric shaped articles of mechanical property such as tensile strength, flexural strength, spring rate and shock resistances.
For example, can be by making above-mentioned fiber lamination and even being embedded on the melts of thermoplastic resin of ethylene series resin etc., obtain all good fiber-reinforced resin formed bodys such as the mechanical property of snappiness rate, high strength, shock resistance, creep resistant etc. and in light weight, electrical specification.In addition, make this fiber in the restrictive condition laminated so that be embedded in stiffening temperature on the monomer of the heat embrittlement polymkeric substance below 220 ℃ or performed polymer after, by sclerosis, can obtain all good fiber-reinforced resin formed body of mechanical property of tensile strength, flexural strength, spring rate, shock resistance etc.Particularly, by mode of the present invention, can obtain the fiber-reinforced resin formed body that combines with the thermosetting polymkeric substance, have and surpass 150 ℃ the stiffening temperature that polyethylene fibre in the past can not reach fully.
In addition, make this fiber under restrictive condition, lamination so be embedded in curing temperature on the unvulcanized rubber below 220 ℃ after, by crosslinked, can obtain all good fiber-reinforced rubber formed body of mechanical property of tensile strength, flexural strength, spring rate, shock resistance etc.Particularly, by mode of the present invention, can obtain and rubber bonded fiber-reinforced rubber formed body, it has 150 ℃ the curing temperature that can not reach fully above polyethylene fibre in the past.
Fibre reinforced polymeric shaped articles
In an example of the fibre reinforced polymeric shaped articles of the present invention shown in Fig. 6, said formed body 1 by processing temperature the matrix 2 of the polymkeric substance below 220 ℃ with in said matrix 2, lay or form with the enhancement layer 3 of said matrix 2 laminated molecular orientation and silane-crosslinked ultra-high-molecular-weight polyethylene fiber.Said fiber-reinforced layer 3 also can be arranged to one deck or the multilayer more than two layers.Concerning specific examples shown in Figure 6, fiber-reinforced layer 3 fully is laid in the matrix of polymkeric substance, and two surperficial 4a, 4b of formed body in fact only are made up of polymkeric substance.Shown in the specific examples of Fig. 7, fiber-reinforced layer 3 also can be laminated under the whole form side of surperficial 4a, 4b or both sides or near existence it with polymeric matrix.
In the fibre reinforced polymeric shaped articles of the present invention, constitute in store in fact its oriented crystalline structure of silane-crosslinked ultra-high-molecular-weight polyethylene fiber of fiber-reinforced layer 3.Said enhancement layer 3 is laid and even is laminated to the front of formed body 1, and by at least one axial molecular orientation and the long filament band of silane-crosslinked ultra-high-molecular-weight polyethylene or the tNonwovens of being made up of this long filament along formed body, fabric or knotwork constitute.
The ratio of fiber-reinforced layer and polymeric matrix has very big variation according to factors such as purposes and thickness.In general, fiber-reinforced layer accounts for 20～80% of cubic capacity, preferably accounts for 40～70%.
When the volumetric ratio of fiber-reinforced layer during less than above-mentioned scope, then the raising of creep properties etc. is just few owing to fiber reinforcement makes tensile strength, flexural strength, spring rate, shock resistance, if and volumetric ratio then just is difficult to form whole fibre reinforced polymeric moulded products greater than above-mentioned scope.
Enhancement layer
Molecular orientation that the present invention uses and silane-crosslinked ultra-high-molecular-weight polyethylene fiber are to contain limiting viscosity (η) and be the above ultrahigh molecular weight polyethylene(UHMWPE) of 5dl/g by making, the composition thermoforming of silane compound radical initiator and thinner, the forming composition of the ultrahigh molecular weight polyethylene(UHMWPE) of grafted silane compound is extended, in extension or after extending, silicon alcohol condensation catalyst is immersed in the elongation moulding body of said forming composition, then makes said elongation moulding body contact crosslinked the making with moisture content.
So-called ultrahigh molecular weight polyethylene(UHMWPE) (A) refers to limiting viscosity (η) under 135 ℃ of naphthalane solvents more than 5dl/g, is preferably 7～30dl/g.
So-called such ultrahigh molecular weight polyethylene(UHMWPE), refer to by ethene or ethene and a spot of other alpha-olefin, for example propylene, 1-butylene, 4-methyl-1-pentene, 1-hexane etc. are in the resulting polyethylene of so-called Ziegler polymerization by polymerization, and molecular weight is in the high scope.
In addition, as the silane compound that crosslinking Treatment is used, can be any silane compound that can be used for grafting processing and crosslinking Treatment, this silane compound has the organic group and the hydrolyzable organic group both sides of free redical initiated polymerization,
Following is general expression
RnSiY
4-n……（1）
In the formula, R is that the unsaturated ethylene that contains the free redical initiated polymerization is an organic group,
Y is hydrolyzable organic group,
N is 1 or 2.
It is that the ethene that contains of unsaturated alkyl, propenyloxy group alkyl, metacryloxy alkyl etc. is the unitary alkyl of esters of unsaturated carboxylic acids etc. that the free radical polymerization organic group has such as ethene such as vinyl, allyl group, butenyl, cyclohexenyls, and more suitable be vinyl.Hydrolyzable organic group has such as alkoxyl group and acyloxy etc.
Suitable silane compound is not limited to this, also has vinyltriethoxysilane, vinyltrimethoxy silane, vinyl three (methoxy ethoxy) silane etc.
At first, by make the composition thermoforming that contains above-mentioned ultrahigh molecular weight polyethylene(UHMWPE), silane compound, radical initiator and thinner carry out silane grafting and moulding with methods such as melt extruded.Promptly produce from the grafting of free radical to the ultrahigh molecular weight polyethylene(UHMWPE) of silane compound.
As radical initiator, can use used radical initiator, for example organo-peroxide, organic peracid ester, Diisopropyl azodicarboxylate, dimethyl azo-bis-isobutyrate on this grafting is handled fully.In order to carry out grafting effectively under the melting mixing condition of ultrahigh molecular weight polyethylene(UHMWPE), the half life temperature of radical initiator is preferably 100～200 ℃.
In order to make silane grafting ultrahigh molecular weight polyethylene(UHMWPE) melt molding, in above-mentioned composition, be equipped with thinner.What be used as such thinner is the solvent of ultrahigh molecular weight polyethylene(UHMWPE) and the various waxs that ultrahigh molecular weight polyethylene(UHMWPE) had intermiscibility.
Per 100 portions of ultrahigh molecular weight polyethylene(UHMWPE)s that (weight) is above-mentioned, preferably using silane compound is 0.1～10 part (weight), particularly 0.2～5.0 part (weight), radical initiator is a catalytic amount, generally be 0.01～3.0 part (weight), particularly 9900～33 parts of 0.05～0.5 part (weight) and thinners (weight), particularly 1900～100 parts (weight).
Melting mixing generally carries out under 150～300 ℃, is preferably under 170～270 ℃ to carry out.Cooperation can be with enjoying the Xie Er mixing machine, and the dry type of V-mixer etc. is mixed, and perhaps also available single shaft or multishaft extruder carry out melting mixing.
Molten mixture is pushed by spinning nozzle, form long filament.At this moment, can the melts that squeeze out from spinning nozzle be drawn, promptly stretch from molten state.The extrusion speed V of molten resin in nib
0With the ratio of the circumvolution speed V of not extension behind the cooling curing can be with following ratio of drawing formula definition.
Ratio of drawing=V/V
0(2)
Such ratio of drawing is that poly molecular weight is decided according to the temperature and the supra polymer of mixture, more than 3, is preferably in more than 6 usually.
Not extending filament to gained carries out prolonged treatment.The extension of silane grafted polyethylene long filament is generally carried out under 40～160 ℃, and special hope is carried out under 80～145 ℃.Any conduct that can use air, water vapor, liquid medium is to make extending filament not remain on thermal medium in the above-mentioned temperature.Yet, as thermal medium, as use a kind of solvent that above-mentioned thinner elution is removed, and its boiling point is also higher than the fusing point of formed body composition, be naphthalane, decane, lam-oil etc. concretely, extend operation, when then may remove above-mentioned thinner, also may eliminate the extension inequality when extending and reach high-elongation.
Extending operation can carry out with the multisegment mode more than a section or two sections.Extension ratio is also relevant with desired molecular orientation effect, but if extend operation generally with 5～80 times, special 10～50 extension ratio carries out, and then can obtain satisfied result.
In above-mentioned extension or after extending, make and flood silicon alcohol condensation catalyst in the forming composition, the elongation moulding body is contacted carry out crosslinked with moisture.
As silicon alcohol condensation catalyst, it itself is known can using, for example the dicarboxylic acid dibutyl tin of dibutyl tin laurate, dibutyltin diacetate, two sad dibutyl tins etc.; The organic titanate of tetrabutyl titanate etc.; Zinc naphthenate.These silicon alcohol condensation catalysts are being dissolved under the state of liquid medium, by contacting with not elongation moulding body or elongation moulding body, can flood these formed bodys effectively.For example, in liquid medium, carry out when prolonged treatment, extend with in the liquid medium, when extending operation, can carry out dip treating the formed body of silicon alcohol condensation catalyst by silicon alcohol condensation catalyst is dissolved in.
Pickup to the silicon alcohol condensation catalyst in the formed body can be so-called catalytic amount, be difficult to the directly concrete amount of regulation, but in the liquid medium that the formed body with not extension or extension contacts, general 10～100%(weight of adding), 25～75%(weight particularly) silicon alcohol condensation catalyst, by this liquid medium is contacted with long filament, can obtain satisfied result.
The crosslinking Treatment of elongation moulding body is that the elongation moulding body of silane grafting ultrahigh molecular weight polyethylene(UHMWPE) by the dipping silicon alcohol condensation catalyst contacts with moisture content and carries out.Favourable crosslinking Treatment condition is under 50～130 ℃ of temperature, makes the elongation moulding body contact 3～24 hours with moisture content.For this reason, moisture content preferably acts on the elongation moulding body with hot water or hot water and steam form.When crosslinking Treatment, the elongation moulding body is placed under the restrictive condition, lax to prevent orientation, perhaps on the contrary also can be under unrestricted condition, the orientation that it is produced to a certain degree is lax.
After the elongation moulding body crosslinking Treatment,, then can also improve tensile strength if carry out prolonged treatment (usually below 3 times) again.
Under restrictive condition, molecular orientation that the present invention uses and silane-crosslinked ultra-high-molecular-weight polyethylene fiber have astonishing characteristics, promptly original with ultrahigh molecular weight polyethylene(UHMWPE) crystalline melting temperature (Tm) is compared, and watery fusion peak value (Tp) is under the high far away temperature.
The original crystalline melting temperature of ultrahigh molecular weight polyethylene(UHMWPE) can once melt postcooling fully with this fiber, made the molecular orientation in the formed body lax, and then made the method for its intensification, promptly obtained with the second trial in the so-called differential scanning calorimetry.
As indicated in above-mentioned Fig. 1, the long filament that the present invention uses has following feature, promptly under the high at least 10 ℃ of temperature of the crystalline melting temperature more original (Tm) than ultrahigh molecular weight polyethylene(UHMWPE), at least have two watery fusion peak values (Tp), and account for more than 40% of whole fusing heats based on the fusing heat of this watery fusion peak value (Tp), particularly more than 60%.
In general, often with two kinds of expressions of Tm+35 ℃ of temperature range～Tm+120 ℃ high temperature side fusing peak value (Tp1) and temperature range Tm+10 ℃～Tm+35 ℃ low temperature side peak value (Tp2), the fusing peak value of Tm itself is quite little for the watery fusion peak value (Tp) of the fiber that the present invention uses.
High temperature side melt portions (Tp1), in the silane grafting amount of formed body after a little while, clear and definite peak value does not appear on melting curve, and most high temperature sides in broad peak value or low temperature side melt portions (Tp2) occur as shoulder or bottom (afterbody) in the scope of Tm+35 ℃～Tm+120 ℃.
When the fusing peak value of Tm is minimum, the fusing peak value shoulder that is hidden in (Tp1) is also arranged, situation about can't confirm.Even if the fusing peak value of Tm does not occur, the function of ultrahigh molecular weight polyethylene(UHMWPE) long filament is also had not a particle of obstruction.The high temperature side fusing peak value (Tp1) of Tm+35 ℃～Tm+120 ℃ and temperature range Tm+10 ℃～Tm+35 ℃ low temperature side melts peak value (Tp2) respectively according to the modulation condition and the Measurement of melting point condition of sample, also is further divided into plural fusing peak value.
These high watery fusion peak values (Tp1, Tp2) have play a part to make the thermotolerance of ultrahigh molecular weight polyethylene(UHMWPE) long filament to significantly improve, but help to make strength retention after the pyritous thermal process to improve, and can think high temperature side fusing peak value (Tp1).
Therefore, preferably account for more than 5% of whole fusing heats based on the summation of the fusing heat of the high temperature side fusing peak value (Tp1) of temperature range Tm+35 ℃～Tm+120 ℃, particularly more than 10%.
The summation that melts the fusing heat of peak value (Tp1) based on high temperature side needs only and is satisfying under the situation of above-mentioned value, even high temperature side fusing peak value (Tp1) can not occur as the main peak value is outstanding, promptly become the aggregate of small leak or wide peak value, though make sometimes loss of thermal resistance some, creep resistant is good.
The degree of the molecular orientation in the formed body can be used X-ray diffraction method, and many refractometries, tendency polarisation method etc. are known.Under the situation of the extension crosslinked with silicane long filament that the present invention uses, use for example abundant Ji of Wu, Kubo brightness one youth: the orientation degree of technical chemistry magazine the 39th volume, 992 pages of (1939) detailed described half-widths, promptly use formula:
Orientation degree F=(90 °-H °/2)/(90 °)
(in the formula; H
0Be half-width along the strength distribution curve of the debye ring of sagittal plane the strongest on the equator.）
Defined orientation degree (F) is become more than 0.90 for making it by molecular orientation, and particularly more than 0.95, this is desirable in thermotolerance and mechanical properties.
In 135 ℃ of following p-Xylol, make extension cross moulding body carry out 4 hours elution process, unreacted silane and contained thinner are removed in elution, by carrying out the quantitative assay of Si with weighting method or atomic absorption spectrometry, can obtain the grafting amount of silane.The silane grafting amount of the fiber that the present invention uses is with Si%(weight in the ultrahigh molecular weight polyethylene(UHMWPE)) expression, be starting point with the thermotolerance, be preferably in 0.01～5%(weight), particularly in 0.035～3.5%(weight) scope in.Promptly when grafting amount during less than above-mentioned scope, cross-linking density is just less than situation of the present invention, and in addition, during greater than above-mentioned scope, crystallinity reduces, and it is abundant inadequately that thermotolerance all becomes.
Concerning molecular orientation-crosslinked with silicane fiber that the present invention uses, the crystalline melting temperature that constitutes at least a portion polymer chain of fiber moves to the high temperature aspect as mentioned above significantly, therefore has excellent heat resistance, 160 ℃ of experience, strength retention after 10 minutes the thermal process is more than 80%, be preferably in 180 ℃ of experience, strength retention after 10 minutes thermal processs is more than 60%, particularly more than 80%, and then 200 ℃ of experience, strength retention after 5 minutes thermal processs is more than 80%, it has astonishing thermotolerance, be in the past ultrahigh molecular weight polyethylene(UHMWPE) can not anticipate fully.
The creep resistant of the long filament that the present invention uses is fabulous, for such as in load: 30% breaks load, temperature: the uncrosslinked long filament under 70 ℃ the condition is placed the unit elongation that has after 1 minute more than 50%, and long filament of the present invention is below 30%, even below 20%.
In addition, in load: 50% breaks load, temperature: the uncrosslinked body under 70 ℃ the condition less than 1 minute with regard to tensile failure, the unit elongation that the long filament that the present invention uses was placed after 1 minute is below 20%.
Grafting and crosslinked silicane form because this formed body is by containing, so adhesive property, particularly the adhesive property with various resenes also is good, and this fact will be easier to understand by the following example of reference.
This that form by ultrahigh molecular weight polyethylene(UHMWPE) and have effectively that the long filament of molecular orientation also has the favorable mechanical performance, for example under the shape of extending filament, have above spring rate of 20GPa and the above tensile strength of 1.2GPa.
The filamentary fiber number of molecular orientation crosslinked with silicane long filament is without particular limitation, but considers from intensity, generally wishes in 0.5～20 DENIER, particularly in 1～10 DENIER.
This long filament generally with multifilament, multifilament twisted union yarn line, by its tNonwovens that constitutes, is weaved cotton cloth or the shape of woven cloth, as the fiber-reinforced layer of thermoplastic resin.
Polymeric matrix
ⅰ) thermoplastic polymer
Its fusing point of matrix thermoplastic polymer that the present invention uses or softening temperature should be below 220 ℃.If fusing point or softening temperature surpass 220 ℃, then molecular orientation in fiber-reinforced resin or type body and silane-crosslinked ultra-high-molecular-weight polyethylene fiber will lose the structure of its oriented crystalline in itself.It is 100～200 ℃ that the fusing point of used matrix thermoplastic polymer or softening temperature require, particularly 150～180 ℃.
Low as having of the matrix polymer that is fit to, in or high density polyethylene(HDPE), the independent polymkeric substance or the multipolymer of crystalline alkene such as LLDPE, polypropylene, crystallinity propylene-ethylene copolymers, propene-1-butene-1 multipolymer, ethene-1-Butylene copolymer, ethylene-propylene-1-Butylene copolymer; The ethylene series elastomerics of the multipolymer of the conj ugated butadiene of the alpha-olefin of ethylene propylene copolymer rubber, the common diene copolymer rubber of ethylene-propylene-non-, ethene etc. and divinyl etc. or the non-conjugated divinyl of ethylidene norbornene or dicyclopentadiene etc. etc. etc.; Also have, the alkene of ethylene-vinyl acetate copolymer, ethylene-ethyl acrylate copolymer, ethylene-vinyl alcohol copolymer, ethylene-vinyl chloride copolymer, ionomer olefin copolymer etc. and the ethene beyond it are the multipolymer of unsaturated monomer etc.The heat adhesiveness of these ethylene series matrix polymers and fiber-reinforced layer is good especially.
In the making of fiber-reinforced resin formed body, the melt flow rate of used polymkeric substance (ASTMD-1238) requires more than/10 minutes, particularly to restrain more than/10 minutes 5 at 1 gram.
Certainly, operable thermoplastic polymer be not limited only to aforesaid these, if fusing point or softening temperature are in the above-mentioned scope, other polymkeric substance also is fit to, for example the phenylethylene resin series of polystyrene, styrene-acrylonitrile copolymer, styrene-butadiene copolymer, ABS resin etc.; The oxygen containing polymer of flexible vinyl chloride resin vinylidene chloride-propylene copolymer, vinylidene chloride-vinyl chloride copolymer, chlorinatedpolyethylene, ethylene chloride resin etc.; The acrylic polymer of polymethylmethacrylate, methyl methacrylate-ethyl acrylate copolymer etc.; The low melting point polyamide class of nylon-11, PA-12, nylon 6/ nylon 66 multipolymers etc.; Ethene to titanic acid ester/isophthalic acid ester copolymer polyester, ethylene/butylene to low melting points such as titanic acid ester copolymer polyester and even low-softening point polyester etc.
In the polymer thermoplastic matrix that the present invention uses, can sneak into itself known dopant, for example one or more of lubricant and even parting agent, antioxidant, tenderizer and even softening agent, weighting agent, tinting material, whipping agent, linking agent etc. according to known prescription.
ⅱ) thermosetting polymkeric substance
The matrix thermosetting polymkeric substance monomer whose that the present invention uses or the stiffening temperature of polymkeric substance should be below 220 ℃.If stiffening temperature surpasses 200 ℃, then can be from make molecular orientation and its oriented crystalline structure of silane-crosslinked ultra-high-molecular-weight polyethylene fiber loss that constitutes in fact the fiber-reinforced resin formed body.It is 100～200 ℃ that the polymeric stiffening temperature of the thermosetting that matrix is used requires, in particular for 150～180 ℃.
The thermosetting polymkeric substance of using as this matrix that is fit to can be, for example resol, furane resin, xylene formaldehyde resin, ketone formaldehyde resin, urea resin, melamine resin, aniline resin, Synolac, unsaturated polyester resin, phthalic acid diene propyl ester resin, Resins, epoxy, triallyl cyanurate resin, cyanate resin, urethane, silicone resin.
In these thermosetting resins, a kind of preferably is Resins, epoxy, for example bisphenol A type epoxy resin, bisphenol f type epoxy resin, phenol phenolic resin varnish type epoxy resin, cresols phenolic resin varnish type epoxy resin, alicyclic epoxy resin, the resin that obtains as the aliphatic epoxy resin, aliphatic series or the aromatics carboxylic that contain heterocyclic ring epoxy resins, hydrogenolysis bisphenol A type epoxy resin, propylene glycol diglycidylether and tetramethylolmethane polyglycidyl ether etc. and the epichlorohydrin reaction of three-glycidyl based isocyanate and glycolylurea epoxy, contain spiral ring Resins, epoxy.Just have on the Racemic glycidol ether type epoxy of the resultant of reaction of phenol carbon black compound and epoxy chloropropane, the hydroxyl separately-the Racemic glycidol ether type epoxy of the resultant of reaction of allylic diallyl bisphenol cpd and epoxy chloropropane dihydroxyphenyl propane.
These Resins, epoxy generally use its epoxy equivalent (weight) about 70～3300, preferably be about 100～1000, softening temperature (surveying with デ エ ラ Application method) is about 60～150 ℃, preferably is about 65～95 ℃, viscosity (25 ℃) is about 10～30000CPS, preferably is about 1000～15000CPS's.
Certainly, when using Resins, epoxy, generally all use, for example boron trifluoride amine coordination compound, 3rd level amine, the 4th grade of ammonium salt, apholate compound, imidazolium compounds, metal oxide, amide compound, urea compounds, melamine compound, isocyanate compound, cyanate esters, phenol system compound, aromatics or aliphatic amine compound, acid anhydrides, polyamino compound etc. with known stiffening agent.
One of the thermosetting resin that is fit to as other is the phenol resins that is obtained by phenols and the reaction of aliphatics aldehydes, comprising resole that is obtained as the condensation reaction of catalyzer by alkali and the novolac resin that obtained as the condensation reaction of catalyzer by acid.The former is generally aqueous or pasty state, is suitable for sneaking into other composition post-hardening.And the latter's importance is conditioned reaction fully, to keep the state of prepolymer.The general viscosity of using (25 ℃) of this phenolic resin is about 100～10000CPS, preferably is about 200～5000CPS, and softening temperature is about 50～150 ℃, preferably is about 70～110 ℃.
As the stiffening agent that the phenolic varnish type phenol resins is used, can adopt general used urotropin, Paraformaldehyde 96, first rank novolac type phenol resin etc.
The another kind that is suitable as thermosetting resin is a polyimide resin, is with general expression R-(NH
2)
nThe expression polyamine (in the formula, R is the divalent organic group, and n is the integer more than 2) and with general expression
The mixture of the unsaturated bismaleimides (PVC ス マ レ ィ ミ De) of expression (in the formula, A is for having the organic group of 2 carbon atoms at least, and m is 2～4) or their preparatory response thing.
As polyamine for example have cyclohexane diamine, Ursol D, 4,4 '-diaminodiphenylmethane, 4,4,4 '-diamino benzophenone, 4,4, xylylene diamines etc.The for example N that has as unsaturated bismaleimides, N '-benzene bismaleimides, N, N '-hexanaphthene bismaleimides, N, N '-methylene radical-2-P-benzene bismaleimides, N, N '-oxo-2-P-benzene bismaleimides, N, N '-4,4 '-the benzophenone bismaleimides, N, N '-P-sulfobenzide maleimide, N, N '-(3,3 '-dimethyl)-methylene radical-2-P-benzene bismaleimides, N, N '-4,4 '-dicyclohexyl methyl hydride bismaleimides, N, N '-m(or P)-the xylylene bismaleimides, N, N '-(3,3 '-diethyl)-methylene radical-2-P-benzene bismaleimides, N, N '-m-cresylene bismaleimides etc.These unsaturated bismaleimidess can also be replaced 60%(weight with single maleimide compound of N-allyl group maleimide, N-propyl group maleimide, N-hexyl maleimide, N-phenylmaleimide etc.) used.
The versamid 900 that is formed by its various composition modulation can also be used in combination with the vinyl monomer of the epoxy group(ing) that contains above-mentioned various Resins, epoxy or epihydric alcohol acrylic ester, epihydric alcohol methylpropenoic acid ester, glycidyl allyl ether etc.
Unsaturated polyester resin as one of hardening resin that is fit to, can add for example reactant of (a) polyvalent alcohol and polycarboxylic acid, has α, β-unsaturated link(age), and be that acid number is at the unsaturated polyester resin below 25, (b) energy and vinylbenzene, Vinylstyrene, Alpha-Methyl benzene allylic alkylation () acrylate, ethylene glycol bisthioglycolate () vinyl monomer of the unsaturated polyester resin copolymerization of acrylate etc., (c) dicumyl peroxide, the radical polymerization initiator of benzoyl peroxide etc. and (d) composition that constitutes of the various one-tenth branch of the promotor of the cobalt naphthenate of usefulness etc. in case of necessity.
In the thermosetting polymeric matrix that the present invention uses, can be according to known prescription, add itself known Synergist S-421 95, for example lubricant and even parting agent, oxidation inhibitor, tenderizer and even softening agent, filling agent, tinting material, whipping agent, linking agent etc. a kind of or more than two kinds.
ⅲ) vulcanized rubber
The vulcanized rubber that the matrix that the present invention uses is used, the curing temperature of its unvulcanized rubber should be below 220 ℃.If curing temperature surpasses 200 ℃, then molecular orientation that is incorporated in the fiber-reinforced rubber formed body and silane-crosslinked ultra-high-molecular-weight polyethylene fiber will substantially lose its oriented crystalline structure.The curing temperature that the used rubber of matrix requires is 100～200 ℃, in particular for 150～180 ℃.
The rubber of using as this matrix that is fit to for example have natural rubber (NR), styrene butadiene base rubber (SBR), nitrile rubber (acrylonitrile butadiene base rubber: NBR), bivinyl rubber (BR), polyisoprene rubber (IR), chloroprene rubber (CR), thiorubber, urethanes, acrylic rubber, isobutylene-isoprene copolymer (IIR), chlorosulphonation rubber, ECD, viton, silicon rubber, ethene ethylene-propylene rubber(EPR) (EPM.EPR), ethylene, propylene diene rubber (EPDM, EPT), ethylene butene rubber, ethylene butene diene rubber etc.
In the rubber that the present invention uses, according to known prescription, can allocate itself known Synergist S-421 95 in advance into, for example sulphur, vulcanization accelerator, vulcanization aid, lubricant, carbon black, stearic acid, zinc oxide, talcum, potter's clay, lime carbonate, silica, oxidation inhibitor), weather-proof stablizer, processes be with a kind of in oil, binding agent, pigment, whipping agent, the organo-peroxide etc. or more than two kinds.
Making method.
Formed body of the present invention is with the fiber-reinforced layer of the above-mentioned various forms of configuration on the face and such as under the restricted state in its end at least, makes with above-mentioned polymkeric substance integrator by making it.That is, for thermoplastic resin, can with the melts integrator after solidify again.For thermosetting resin, can make it and monomer and even prepolymer integrator, in its post-hardening.For rubber, make with the unvulcanized rubber integrator at revulcanization and even crosslinked thereafter.
The combination of fiber-reinforced layer and thermoplastic resin melts can in all sorts of ways and finish.For example, make the film of preformed thermoplastic resin and even sheet material and fiber-reinforced layer superimposed, in thermoplastic resin fusing, promptly substantially keep pressing the described applications as laminates of knot under the temperature of oriented crystalline structure of the superhigh molecular weight polyethylene fibers in the toughener layer.Press the knot operation as hot pressing, to carry out, can also resemble and carry out continuously the hot roll extrusion with intermittent type and even semi continuous.When pressing the knot operation, importantly make the end of fiber-reinforced layer restricted, for example, in advance fiber roll around press with making the end restricted on the substrate, perhaps when pressing the knot operation, reach by on fiber-reinforced layer, applying suitable tension force.When fiber is a machinery when arranging vertically and with the vertical rectangular direction of machinery, can on its two directions, apply the tension force of not allowing that the fiber free shrink is such.
Additive method can make the extrudate of the molten state that is in thermoplastic resin and fiber-reinforced layer superimposed, presses knot to make its integrator again.For example, be squeezed into thermoplastic resin between the bilaminar fiber enhancement layer, make their integrators again, perhaps the fiber-reinforced layer to two individual layers is squeezed into thermoplastic resin, makes its integrator again.Certainly, multiwalled fiber-reinforced layer and multiwalled thermoplastic resin extrudate are superimposed, press knot again, synthesize one.
The monomer of fiber-reinforced layer and thermosetting polymkeric substance or the zoarium of prepolymer solidify the realization that can in all sorts of ways.For example, make the film of the prepolymer that is in semi-harden B state in advance and even sheet material and fiber-reinforced layer superimposed, then make the prepolymer cures of Thermocurable polymkeric substance, but to substantially keep under the temperature of oriented crystalline structure of the ultrahigh molecular weight polyethylene(UHMWPE) in the enhancement layer, make this applications as laminates press knot to solidify.Other condition is all in accordance with above-mentioned method.
Another method, make after fiber-reinforced layer is immersed in the monomer of thermosetting polymer or the prepolymer, the monomer of thermosetting polymer or prepolymer cures, but to substantially keep under the temperature of oriented crystalline structure of the superhigh molecular weight polyethylene fibers in the enhancement layer, make impregnated fiber-reinforced layer with individual layer or multilayer build-up and press knot to solidify again.
The crosslinked realization that ins all sorts of ways of the combination of fiber-reinforced layer and unvulcanized rubber.For example, make the film of the blending rubber after mixing with linking agent etc. in advance and even sheet material and fiber-reinforced layer superimposed, fusion rubber cross then, but to substantially keep said applications as laminates being pressed making friends with connection under the temperature of oriented crystalline structure of the superhigh molecular weight polyethylene fibers in the enhancement layer.
Fibre reinforced polymeric shaped articles of the present invention is not limited to the secondary circle shape.For example, shape with tNonwovens, fabric or the knotwork of long filament or this long filament is configured to tubulose to fiber-reinforced layer, by the plectane mould with the tubular extrusion thermoplastic resin, in above-mentioned mould or outside the mould, both are integrated, perhaps make prepolymer and even the monomer coating and even the dipping of thermosetting polymkeric substance, perhaps rubber-coated, then can obtain the piped fibre reinforced polymeric shaped articles.As fuse,, then can form the foreskin of fiber strengthening formed body with electric wire and optical cable if adopt above-mentioned forming method.
The present invention makes molecular orientation and silane-crosslinked ultra-high-molecular-weight polyethylene fiber under restrictive condition.Become one with multiple polymers, can state with the oriented crystalline structure that keeps above-mentioned fiber in the matrix of above-mentioned polymkeric substance in fact under, it is existed as fiber-reinforced layer.
So this formed body has the good tensile property of above-mentioned fiber, this in addition fiber is owing to be by the silane conversion, not only with polyethylene, with other polymeric cohesiveness also be good, and can obtain snappiness rate, high-intensity formed body.
When using polyolefin substrate, electric insulating quality is good, compares with the matrix that uses Resins, epoxy and unsaturated polyester resin, and dielectric loss is also few, and electric property is good.
Have, during with the vulcanized rubber matrix, this fiber can obtain snappiness rate, high-intensity formed body, applicable to high pressure hose, the cloth that tows the head, tire and women's articles for use because the silane conversion is also good with the cohesiveness of vulcanized rubber again.
Below, will be described more specifically the present invention in conjunction with the embodiments, but under the situation that does not surmount main points of the present invention, the present invention is not limited to these embodiment.
＜crosslinked with silicane extends the making of superhigh molecular weight polyethylene fibers 〉
Grafting and spinning
Make with respect to the ultrahigh molecular weight polyethylene(UHMWPE) (powder of limiting viscosity [η]=8.26dl/g): the vinyl triethoxyl disilane of 100 parts (weight) (SHIN-ETSU HANTOTAI's chemistry is made): 10 parts (weight) and 2,5-dimethyl-2, (the Japanese grease manufacturing: trade(brand)name of 5-two (tert-butyl peroxide) hexane, パ ヘ Ha キ サ 25B): after 0.1 part of (weight) uniform mixing, in ultrahigh molecular weight polyethylene(UHMWPE) 100 parts (weight), add (the Japanese smart wax manufacturing of paraffin powder, trade(brand)name, Le バ ッ Network ス 1266. fusing points=69 ℃): 370 parts (weight) and mixing obtain mixture.Then, (screw diameter=20 millimeter L/D=25) with said mixture, are carried out fusion and are mixed under 200 ℃ that set, be that 2 millimeters mould makes this melts be spun into silk by die throat diameter again, finish the silane grafting with screw extruder.Spinning fibre is with 180 centimetres air gap, and cooling curing in air at room temperature is made and do not extended ultrahigh molecular weight polyethylene(UHMWPE) silane grafted fibre.This extension silk is 800 DENIER, and the ratio of drawing during spinning is 36.4.At this moment winding speed is 90 meters/minute.
The mensuration of silane grafting amount
About 8 grams of the not extension grafted fibre that use above-mentioned method to make, fusing in 200 milliliters of the p-Xylol of 135 ℃ of following heat tracings.Then, ultrahigh molecular weight polyethylene(UHMWPE) is separated out in the ethane of surplus, remove paraffin and unreacted silane compound.Afterwards, with weighting method with Si%(weight) the grafting amount obtained is 0.57%(weight).
With above-mentioned method the not extension fiber of grafting that is spun into silk by the ultrahigh molecular weight polyethylene(UHMWPE) mixture is extended under the following conditions, obtain the directed fiber that extends.With three deflector rolls, carrying out two sections extensions in as the extension slot of thermal medium with n-decane.At this moment, temperature is 110 ℃ in first extension slot, and temperature is 120 ℃ in second extension slot, and the useful length of groove is respectively 50 centimetres.During extension, the rotating speed that makes first deflector roll is 0.5 meter/minute, by changing the rotating speed of the 3rd deflector roll, obtains the fiber of desired ratio of elongation.The rotating speed of second deflector roll is made appropriate selection in stablizing the scope of extending.But ratio of elongation is calculated and is obtained by the rotating ratio of first deflector roll and the 3rd deflector roll.
The fiber of gained in decompression under the room temperature drying make and extend ultrahigh molecular weight polyethylene(UHMWPE) silane grafted fibre.
The dipping of crosslinking catalyst
Directional fiber to the silane compound grafting ultrahigh molecular weight polyethylene(UHMWPE) made of aforesaid method further carries out under the crosslinked situation, during extension in the 2nd extension slot with n-decane and with the mixture of two lauric acid dibutylester tin of n-decane equivalent as thermal medium, in elution paraffin, two lauric acid dibutylester tin are immersed in the fiber.The fiber of gained is dry until no decane stink under the room temperature in decompression.
Crosslinked
After this, fiber was placed in boiling water 12 hours, finished crosslinked.
The mensuration of gelling ratio
About 0.4 gram is put in the Erlenmeyer flask with the crosslinked with silicane extension superhigh molecular weight polyethylene fibers that aforesaid method obtains, and this bottle is provided with the condenser that has added 200 milliliters of p-Xylol, stirs 4 hours under boiling state.Then, the 300 order metallic screens made from stainless steel filter insolubles.Under 80 ℃ of decompressions after the drying, weighing and obtain the weight of insolubles.Obtain the gelling ratio by following formula.
Gelling ratio=(weight of insolubles)/(sample weight) * 100(%)
The gelling ratio of the above-mentioned sample of making is 51.4%.
Tensile elasticity rate, tensile strength and breakpoint extensibility at room temperature use ィ Application ス ト ロ ソ universal testing machine 1123 types (manufacturing of ィ Application ス ト ロ ソ company) to measure.Sample length between anchor clamps is 100 millimeters, and draw speed is 100 millimeters/minute.But tensile elasticity rate is the initial stage spring rate.Making density of pe is 0.96 gram/cubic centimetre, measures the weight and the length of fiber, and it is long-pending to calculate the fiber cross section of obtaining necessity.
Table 1 is depicted as the rerum natura of the crosslinked with silicane extension superhigh molecular weight polyethylene fibers of gained thus.
Table 1
Test portion test portion-1
Fiber number 8.3 DENIER
19.4 times of extension ratios
Intensity 1.55GPa
Spring rate 40.1GPa
Unit elongation 7.5%
The original crystalline melting temperature of obtaining as the main fusing peak value of secondary temperature elevation (Tm) of ultrahigh molecular weight polyethylene(UHMWPE) is 132.2 ℃, accounts for the ratio of holocrystalline fusing heat and is respectively 73% and 22% based on the ratio that the fusing heat of Tp1 accounts for holocrystalline fusing heat based on the fusing heat of Tp.At this moment, Tp2 is mainly 151.0%, and Tp1 is mainly 226.5 ℃.The evaluation creep test of creep properties adopts thermal stress strain determinator TMA/SS10(electronic industry Co., Ltd. to make), long 1 centimetre of sample, atmosphere temperature is 70 ℃.Figure 8 shows that the result under 30% load of crushing load.Compared by the crosslinked with silicane extension superhigh molecular weight polyethylene fibers (sample-1) of present embodiment making and the following extension superhigh molecular weight polyethylene fibers of making of comparative example 1 (sample-2), creep properties all increases significantly.
Under 70 ℃ of atmosphere temperatures, carry out creep test with 50% the load that is equivalent to crushing load under the room temperature, the unit elongation after the loading after 1 minute, 2 minutes and 3 minutes is shown in table 2.
Table 2
Test portion time (branch) unit elongation (%)
Test portion-1 1 7.4
2 8.2
3 8.6
Close-burning evaluation
Carry out close-burning evaluation with the traction method.Agglutinating object resin is Resins, epoxy (Resins, epoxy, Showa Highpolymer Co., Ltd makes), uses fast method, is undertaken by the cohesive force A method of JIS L-1017 man-made fiber tire thread test method.Strength retention thermal process test after the thermal process is placed in the open type transmission mechanism (unlimited fully: as field leaf well making made) to carry out.It is 3 meters that sample is about, and can be provided with the method by turning back on the device of a plurality of pulleys at the two ends of stainless steel framework, and the sample two ends are fixed.At this moment, the sample two ends are not fixed to so that sample is lax and are as the criterion, and do not add tension force to sample on one's own initiative.It the results are shown in table 3.(table 3 is seen the literary composition back)
As shown in Table 3, used crosslinked with silicane extension superhigh molecular weight polyethylene fibers has astonishing high-temperature capability persistence in the present embodiment.By X-ray diffraction measure the orientation degree fiber be in the anchor clamps of ホ Le ダ-type around 10～20 circles, the one side is cut off, be pencil and use for measuring.Degree of orientation is polyethylene crystalline face (110) reflection that occurs on the line under the line with the deflector instrumentation, obtains reflection strength and distributes.Calculating is to carry out according to above-mentioned Wu messieurs' method.The orientation degree of trying to achieve is 0.955.
The moulding of＜fiber-reinforced resin formed body 〉
With high-density polyethylene powder (limiting viscosity [η]=2.3dl/g, 127 ℃ of fusing points) as the matrix resin.The crosslinked with silicane that employing is made by above-mentioned method extends superhigh molecular weight polyethylene fibers as reinforcing fiber.Obtain the fiber-reinforced resin formed body by following method.In 150 * 150 millimeters square stainless steel frame, periphery is wide 1.5 millimeters, and 1 millimeter of thickness extends superhigh molecular weight polyethylene fibers to above-mentioned crosslinked with silicane and amounts to 8 layers by reeling in the orthogonal direction table alternately.At this moment, each adjacent fibres will engage each other closely in each layer, but will manage not make it superimposed.Afterwards, the above-specified high density polyethylene powders that extends weight such as superhigh molecular weight polyethylene fibers with the laminated crosslinked with silicane of needs is placed on the metal frame space segment laminate surface equably, clamp said metal frame with two stainless steel plates.Then use heated press, 170 ℃, heating in 6 minutes, pressurization.Pressure should be modulated to 50 kg/cm during pressurization.Afterwards, moulding is promptly finished in the cooling of water chilling press.
Then, excision around the metal frame central space part, the sample of using as physical property measurement.
The thickness of sample is 1.5 millimeters, and it is the 50%(volume that crosslinked with silicane extends the ultra-high molecular weight fibre content).At room temperature (23 ℃) are according to JISK6911(ASTMD790), on ィ Application ス ト ロ ソ universal testing machine 1123 types (ィ Application ス ト ロ ソ corporate system), carry out the crooked elastic rate of this sample, the mensuration of flexural strength.At this moment, the test film sample is 50 * 25 millimeters bend specimen rectangle dumb-bell shapes, and the said sample wire drawing is modulated into and the fiber orthogonal.Table 4 is depicted as the flexural strength and the crooked elastic rate of gained sample.
Table 4
Test portion flexural strength crooked elastic rate
GPa GPa
Test portion-A 0.043 2.13
According to JIS K6760(ASTM D638-68) measure tensile yield strength, tensile elasticity rate.But test piece at this moment is by using JIS2 Evil bell shape, above-mentioned sample being punched on the direction that becomes orthogonal with fiber make.It the results are shown in table 5.
Table 5
Test portion tensile yield strength tensile elasticity rate
GPa GPa
Test portion-A 0.123 23.3
Compare with following comparative example 2, surmount the high-temperature molding of general knowledge of polyethylene fibre after, showed already, also given full play to the effect of reinforcing fiber.
The formation of＜fiber-reinforced resin formed body 〉
Use polypropylene powder (limiting viscosity [η]=2.0dl/g, fusing point=160 ℃) as the matrix resin.Extend superhigh molecular weight polyethylene fibers as reinforcing fiber with the crosslinked with silicane of making as embodiment 1 described method.Under the following conditions, make the moulding of fiber-reinforced resin formed body.In 150 * 150 millimeters square stainless steel frame, 15 millimeters of periphery width, 1 millimeter of thickness extends superhigh molecular weight polyethylene fibers to above-mentioned crosslinked with silicane and press 8 layers of the totals of reeling in the staggered face of land of orthogonal direction.At this moment, each adjacent fibres will engage each other closely in each layer, but not superimposed.Afterwards, the above-mentioned polypropylene powder that extends weight such as superhigh molecular weight polyethylene fibers with the laminated crosslinked with silicane of needs placed metal frame space segment lamination and on, clamp said metal frame with two stainless steel plates, use heated press, 180 ℃ of pressurization, heating, 6 minutes.At this moment pressure is 50 kg/cm.Then, with the cooling of water-cooled press, finished moulding.The thickness of the fiber-reinforced resin formed body of gained is 1.5 millimeters.It is the 47%(volume that this crosslinked with silicane extends superhigh molecular weight polyethylene fibers content).Press crooked elastic rate, the flexural strength of this fiber-reinforced resin formed body of embodiment 1 described method mensuration, be shown in table 6.
Table 6
Test portion flexural strength crooked elastic rate
GPa GPa
Test portion-B 0.057 8.27
Table 7 is depicted as tensile yield strength, the tensile elasticity rate of measuring with embodiment 1 described method.
Table 7
Test portion tensile yield strength tensile elasticity rate
GPa GPa
Test portion-A 0.273 36.1
Comparative example 1
Ultrahigh molecular weight polyethylene(UHMWPE) extends the making of fiber
With embodiment 1 described method, with the powder of ultrahigh molecular weight polyethylene(UHMWPE) (limiting viscosity [η]=8.20): 100 parts (weight) and as embodiment 1 described paraffin powder: 320 parts (weight) are spun into silk.At this moment ratio of drawing is 25 times, and the fiber number of not extending silk is 1000 DENIER.Then carry out identical extension, obtain extending fiber.The rerum natura of gained fiber is shown in table 8.(table 8 is seen the literary composition back)
The fusing characteristic curve of this fiber (test portion-2) is shown in Fig. 3.The original crystalline melting temperature Tm that main fusing peak value when heating up with the second time is tried to achieve is 132.2 ℃.Account for the ratio of holocrystalline fusing heat and be respectively 32.1% and 1.7% based on the fusing heat of Tp based on the ratio that the fusing heat of Tp1 accounts for holocrystalline fusing heat.
With among the embodiment 1＜evaluation of creep properties described in method measure creep properties.It the results are shown in Fig. 8.
In addition, the method identical with embodiment 1 described method carried out the mensuration (atmosphere temperature=70 ℃, 50% load of the crushing load under load=room temperature) of creep properties, loads the back sample and ruptures at once.Cohesive force presses embodiment's 1＜evaluation of cementability described in method measure.Its result is shown in Fig. 9 with embodiment 1.
The mensuration of the strength retention after the thermal process by embodiment 1＜surpass the strength retention after the journey described in method carry out.Place less than 10 minutes fusing fully down 180 ℃ of unlimited temperature.
The moulding of＜fiber-reinforced resin formed body 〉
With embodiment 1 described high-density polyethylene powder as the matrix resin, adopt embodiment 1 described method, use heated press, by 170 ℃, heating in 6 minutes, pressurization, above-mentioned superhigh molecular weight polyethylene fibers laminate is embedded in the above-mentioned high density polyethylene(HDPE), forms the fiber-reinforced resin formed body.After the cooling, order is examined the layer of fibers of formed body inside, and wherein fibers melt is dispersed into striated.The physics of this formed body is identical with the sample-C of following comparative example 2.
Comparative example 2
, use in the heating and pressurizing shaper as the matrix resin with embodiment 1 described high-density polyethylene powder, 170 ℃, 6 minutes heating and pressurizing.Thereafter, pressurization cooling on the cooling pressure forming machine again obtains high density polyethylene(HDPE) compression moulding thing.Measure flexural strength, crooked elastic rate with embodiment 1 described method, it the results are shown in table 9.
Table 9
Test portion flexural strength crooked elastic rate
GPa GPa
Test portion-C 0.027 1.20
Table 10
Test portion tensile yield strength tensile elasticity rate
GPa GPa
Test portion-C 0.023 0.53
Comparative example 3
As the matrix resin, in pressure forming machine, 180 ℃, heating in 6 minutes, pressurization then, in the cooling pressure shaper, are pressurizeed again with embodiment 2 described polypropylene powders, and cooling obtains the polypropylene forming composition.Press embodiment 1 described method and measure flexural strength, crooked elastic rate, it the results are shown in table 11.
Table 11
Test portion flexural strength crooked elastic rate
GPa GPa
Test portion-D 0.038 1.60
Table 12
Test portion tensile yield strength tensile elasticity rate
GPa GPa
Test portion-D 0.037 0.82
The formation of＜fiber-reinforced resin formed body 〉
Use nylon 12 powder (relative viscosity=2.45, fusing point=176 ℃) as matrix resin, use the crosslinked with silicane of making by embodiment 1 described method to extend superhigh molecular weight polyethylene fibers, obtain the fiber-reinforced resin formed body with following method as reinforcing fiber.In 150 * 150 millimeters square stainless steel frame, periphery is wide 15 millimeters, and 1 millimeter of thickness extends superhigh molecular weight polyethylene fibers to above-mentioned crosslinked with silicane and press 8 layers of the totals of reeling in the staggered face of land of orthogonal direction.At this moment, each adjacent fibres will engage each other closely in each layer, but not superimposed.Afterwards, above-mentioned nylon 12 powder of the weight identical with the laminated crosslinked with silicane extension of needs superhigh molecular weight polyethylene fibers are placed on the metal frame laminate surface, clamp said metal frame with two stainless steel plates.In the thermal pressure shaper, at 195 ℃, heating, pressurization 6 minutes.At this moment pressure is 50 kg/cm.Make nylon 12 powder dry in 105 ℃ of following 12 hours nitrogen atmosphere before this earlier.Then, moulding has been finished in the pressurization cooling in the water-cooled pressure forming machine.The thickness of gained fiber strengthening formed body is 1.5 millimeters, and it is the 52%(volume that its crosslinked with silicane extends high molecular weight polyethylene fiber content).Measure flexural strength, the crooked elastic rate of this fiber strengthening formed body by embodiment 1 described method, it the results are shown in table 13.
Table 13
Test portion flexural strength crooked elastic rate
GPa GPa
Test portion-E 0.051 7.20
Table 14
Test portion tensile yield strength tensile elasticity rate
GPa GPa
Test portion-E 0.375 28.4
Comparative example 4
As the matrix resin, in the heated pressure shaper,, in cooling pressurization in the cooling pressure shaper, obtain nylon 12 compression moulding things afterwards with embodiment 3 described nylon 12 powder 196 ℃ of following heating and pressurizing 6 minutes.Press embodiment 1 described method and measure flexural strength, crooked elastic rate, it the results are shown in table 15.
Table 15
Test portion flexural strength crooked elastic rate
GPa GPa
Test portion-F 0.045 1.18
Table 16
Test portion tensile yield strength tensile elasticity rate
GPa GPa
Test portion-F 0.048 1.25
The formation of＜fiber-reinforced resin formed body 〉
(Mitsui petrochemical industry (strain) is made to make 100 gram Resins, epoxy, trade(brand)name=ェ Port ミ ッ Network R-301), 30 gram Resins, epoxy (are made with producer, trade(brand)name=ェ Port ミ ッ Network R-140) 4 gram Dyhard RU 100s and 3 gram N-(3,4-dichloride biphenyl)-N ', N '-dinaphthalene urea is at 33 gram naphthalene methylethylketones and 20 gram N, and varnish is made in fusing in the mixed solvent of N-two naphthoamides.Above-mentioned varnish impregnation is extended on the polyethylene fibre at the crosslinked with silicane of fixing wound at the foregoing description on the stainless steel frame 1, and drying is 30 minutes under 100 ℃, obtains unidirectional prepreg.Then, the prepreg of gained builds up 9 layers in staggered mode, fixes with metal frame all around, through pressure forming in 6 minutes, makes 9 layers veneer sheet under 160 ℃.It is the 58.0%(volume that the crosslinked with silicane of the veneer sheet of gained extends superhigh molecular weight polyethylene fibers content).
At room temperature, according to JIS K6911(ASTM D790) measure crooked elastic rate, the flexural strength of this veneer sheet with 1123 type ィ Application ス ト ロ ソ universal testing machines.At this moment test piece sample becomes 50 * 25 millimeters rectangular specimen by the mode of fiber orthogonal with this veneer sheet machining.The flexural strength and the crooked elastic rate of said sample are shown in table 17.
Table 17
Test portion flexural strength crooked elastic rate
GPa GPa
Test portion-A 0.25 14.2
According to JIS K6760(ASTM D638-68) measure tensile yield strength, tensile elasticity rate.But test piece sample at this moment is by the JIS2 dumb-bell shape, makes above-mentioned veneer sheet is die-cut.It the results are shown in table 18.
Table 18
Test portion tensile yield strength tensile elasticity rate
GPa GPa
Test portion 0.345 3.5
Comparative example 5
The moulding of＜fiber-reinforced resin formed body 〉
Ultrahigh molecular weight polyethylene(UHMWPE) with embodiment 4 described Resins, epoxy and above-mentioned comparative example 1 extends fiber as the matrix resin, obtains unidirectional prepreg by embodiment 4 described methods.Then, the prepreg that makes gained is lamination alternately, with embodiment 4 identical conditions under, make veneer sheet.After the cooling, examine with order, see formed body inside, its fiber fusing as a result loses fiber shape.
The formation of＜fiber-reinforced resin formed body 〉
Table 19
Test portion flexural strength crooked elastic rate
GPa GPa
Test portion-B 0.13 5.60
The same embodiment 4 described methods of pressing are measured tensile yield strength and tensile elasticity rate, and it the results are shown in table 20.
Table 20
Test portion tensile yield strength tensile elasticity rate
GPa GPa
Test portion-B 0.033 6.30
Comparative example 6
Pouring in the metal frame,, obtain the epoxy resin board sample of 1.5 mm thick 160 ℃ of extrusion formings in following 6 minutes by the composition varnish of embodiment 4 usefulness.Press embodiment 4 described methods, measure flexural strength, crooked elastic rate, tensile yield strength and tensile elasticity rate with the sample of gained.It the results are shown in table 21 and table 22.
Table 21
Test portion flexural strength crooked elastic rate
GPa GPa
Test portion-C 0.11 4.73
Table 22
Test portion tensile yield strength tensile elasticity rate
GPa GPa
Test portion-C 0.051 0.70
The formation of＜fiber-reinforced rubber formed body 〉
With the matching component shown in the table 23, with steam water cold type two roller roller presses (the smart mechanism in peace field is done manufacturing for 3 " * 8 ", 191-WM type), to make blending rubber in 30 minutes.At this moment roll surface temperature, preliminary roller are 50 ℃, and back roller is 60 ℃, rotating speed: preliminary roller is 12.6rpm, and back roller is 15.7rpm.The rerum natura of blending rubber is shown in table 24.(table 23,24 is seen the literary composition back)
Use and extend the cloth that interweaves that the multifilament of high molecular weight polyethylene fiber is made into by the crosslinked with silicane made among the embodiment 1 (cloth is organized=interweaved, quality=310 grams/square metre, vertical silk density=23 piece/2.54 centimetres, laterally=2 piece/2.54 centimetres) as reinforcing fiber, be embedded in the above-mentioned stereoregular rubber, by sulfuration, make 2 millimeters fiber strengthening sulfuration sheet material under the following conditions.Interweave cloth around be fixed on around the pressing mold,, on heated press, heated 10 minutes down with 2 millimeters dividing plates at 157.2 ℃.At this moment the pressure that is applied on the sample is 50 kg/cm.Then, on the water-cooled press, cool off, form the fiber-reinforced rubber formed body.The fiber-reinforced rubber formed body of gained is with the JIS3 dumb-bell shape, and is vertically die-cut at crossed fiber, is used for tension test.(model-1123, ィ Application ス ト ロ ソ makes) at room temperature with 500 millimeters/minute draw speed, carried out in tension test on ィ Application ス ト ロ ソ universal testing machine.
Obtain the rerum natura and the hardness of fiber rubber formed body by the JISA method, be shown in table 25 simultaneously.
Table 25
Test portion breaking tenacity tension set hardness
Kgf/cm
2%
1 312 6.5 59
Comparative example 6
Press the matching component shown in the table 24,, make the sulfuration sheet material of 2 millimeters of thickness with the method for embodiment 6.The rerum natura of the sulfuration sheet material of gained is shown in table 26.Rerum natura is pressed embodiment 6 described methods and is measured.
Table 26
Test portion breaking tenacity tension set hardness
Kgf/cm
2%
Add sulphur test portion-2 205 540 56
The formation of＜fiber-reinforced rubber formed body 〉
According to embodiment 6 described device and conditions, make blending rubber with the matching component shown in the table 27.(table 27 is seen the literary composition back)
The rerum natura of gained blending rubber is shown in table 28.(table 28 is seen the literary composition back)
Extend interweave cloth and the above-mentioned blending rubber that superhigh molecular weight polyethylene fibers is made into embodiment 1 described crosslinked with silicane, make thick 2 millimeters fiber strengthening sulfuration sheet material with embodiment 6 described methods.At this moment sulfuration was carried out under 180 ℃ 8 minutes.The rerum natura of gained fiber-reinforced rubber formed body is shown in table 29.(table 29 is seen the literary composition back)
Comparative example 7
With the matching component shown in the table 27, make blending rubber with embodiment 6 described methods.Under embodiment 7 described conditions, make thick 2 millimeters sulfuration sheet materials with the blending rubber of gained.The rerum natura of the sulfuration sheet material of making is shown in table 30.(table 30 is seen the literary composition back)
The formation of＜fiber-reinforced rubber formed body 〉
According to embodiment 6 described device and conditions,, make blending rubber with the matching component shown in the table 31.(table 31 is seen the literary composition back)
Then, extend superhigh molecular weight polyethylene fibers with the blending big shield glue of gained and embodiment 1 described crosslinked with silicane and be made into the cloth that interweaves, make thick 2 millimeters fiber strengthening sulfuration sheet material with embodiment 6 described methods again.At this moment sulfuration was carried out 15 minutes at 150 ℃.The fiber-reinforced rubber formed body of gained is shown in table 32.(table 32 is seen the literary composition back)
Comparative example 8
With the matching component shown in the table 31,, make blending rubber with embodiment 6 described methods.Make thick 2 millimeters sulfuration sheet materials with the blending rubber of gained under embodiment 8 described conditions, the rerum natura of the sulfuration sheet material of making is shown in table 33.(table 33 is seen the literary composition back)
Comparative example 9
(ダ ィ ニ-マ SK60: ダ ィ ニ-マ society makes with extending superhigh molecular weight polyethylene fibers, tensile elasticity rate=80GPa, tensile strength=2.4GPa, multifilament) be made into the cloth that interweaves (cloth tissue=plain weave, quality=295 gram/square metre, silk density=31 piece/2.54 centimetres, identical in length and breadth) as reinforcing fiber, with the blending rubber of the component shown in the table 23,, make the fiber-reinforced rubber formed body with embodiment 6 described methods.The rerum natura of the fiber-reinforced rubber formed body made from method and then the mensuration of embodiment 6, it the results are shown in table 34.(table 34 is seen the literary composition back)
Compare with the rerum natura (table 26) of the base rubber shown in the comparative example 7, its rerum natura obviously reduces, and its reason is a fibers melt.With simple extension high molecular weight polyethylene fiber about 10 minutes thermal process of ability not under 157.2 ℃.
Table 3
Test portion opens wide intensity GPa spring rate GPa unit elongation storage period
Temperature ℃ (min) (conservation rate %) (conservation rate %) (conservation rate %)
Test portion-1 180 ℃ 10 1.53(99) 9.5(126 32.5(81))
200℃ 5 1.40（90） 26.5（66） 10.7（143）
Table 8
Test portion fiber number extension ratio strength, elastic rate unit elongation
28.0 times of 1.68GPa 45.5GPa 6.3% of test portion-2 8.5 DENIER
Table 23
The title complex trade(brand)name is made weight portion of commercial firm
NR ラ バ-ス モ-Network シ-ト #1 シ エ Le chemistry 70
The synthetic go system 41.3 of SBR JSR1778 Japan
GPF カ ヘ Port Application プ ラ Star Network rising sun #55 rising sun カ-Port Application 50
Cycloalkanes acid system oil Circosol 2 * 11 Sun Oil 8
Zinc oxide Zinc Oxide spy Sakai chemical industry 5
Stearic acid-Song Ben grease 1.5
Butylation vinylbenzene cresols Win Stay 100 グ ッ De ィ ャ-1.0
2-[4-morpholinodithio thiamines ァ Network セ Le DM Kawaguchi chemistry 0.85
Vulkacit D ァ Network セ Le D Kawaguchi chemistry 0.15
Rubber is seen chemical industry 2.5 with sulfur flour Jinhua seal micro mist Sulfur crane
Table 24
Test portion ML
1+4(100 ℃) MS
-3(121 ℃)
Cooperate test portion-1 43 22 minute
Table 27
The title complex trade(brand)name is made amount portion of commercial firm
EPDM Mitsui EPT3072E Mitsui petroleum chemistry 70
EPDM Mitsui EPT3070 Mitsui petroleum chemistry 50
Zinc oxide Zinc Oxide spy Sakai chemical industry 5
Stearic acid-Song Ben resin 1
FEF カ-Port Application プ ラ ッ Network rising sun II 60 rising suns カ-Port Application 100
SRF カ-Port Application プ ラ ッ Network rising sun II 50 rising suns カ-Port Application 60
Calcium hydrogen carbonate is heavy charcoal acid カ Le シ ウ system earth house カ オ リ Application industry 40 5.
Paraffin series oil シ ェ Le Off レ ッ ス 491J シ ェ Le chemistry 84
N-cyclohexyl 2-[4-morpholinodithio thiamines ァ Network セ Le CZ Kawaguchi chemistry 0.5
Ethylene thiourea ァ Network セ Le 22 Kawaguchi's chemistry 0.5
Curing tetramethyl-thiuram ノ Network セ ラ-TT imperial palace emerging chemical 0.5
Two-sulfo-nitrogen base methane amide dibutyl tin ァ Network セ Le BZ Kawaguchi chemistry 1.5
Morpholine-disulphide バ Le ノ ッ Network R imperial palace emerging chemical 1.5
Rubber is seen chemical industry 0.5 with sulfur flour Jinhua seal micro mist Sulfur crane
Table 28
Test portion ML
1+4(100 ℃) MS
-3(125 ℃)
T5
Cooperate test portion-2 47 13.8
Table 29
Test portion breaking tenacity tension set hardness
kgf/cm
2% （JIS A）
Add sulphur test portion-3 295 7.8 62
Table 30
Test portion breaking tenacity tension set hardness
kgf/cm
2% （JIS A）
Sulfuration test portion-4 114 460 65
Table 31
The title complex trade(brand)name is made weight portion of commercial firm
The synthetic go system 100 of SBR JSR-1712 Japan
Zinc oxide Zinc Oxide spy Sakai chemical industry 5
SRF カ-Port Application プ ラ ッ Network rising sun # 50 rising sun カ カ-Port Application 50
Kaolin ス-バ-ラ ィ ト Kobe Network レ-50
Fatty acid treatment lime carbonate ノ-ベ ラ ィ ト SS day east efflorescence industry 20
The emerging chemical industry 10 of coumarone resin Network マ ロ Application CL imperial palace
N-cyclohexyl 2-[4-morpholinodithio thiamines ァ Network セ Le CZ Kawaguchi chemistry 1.5
The curing tetramethyl-thiuram ノ Network セ ラ-emerging chemical industry 1.5 of TT imperial palace
Rubber is seen chemical industry 0.5 with sulfur flour Jinhua seal micro mist Sulfur crane
Table 32
Test portion breaking tenacity tension set hardness
kgf/cm
2%
Sulfuration test portion-5 273 6.8 63
Table 33
Test portion breaking tenacity tension set hardness
kgf/cm
2% （JIS A）
Sulfuration test portion-6 114 460 65
Table 34
Test portion breaking tenacity tension set hardness
kgf/cm
2% （JIS A）
Sulfuration test portion-7 73 64 59
Claims (15)
1, fibre reinforced polymeric shaped articles, it is characterized in that said formed body is made up of at the matrix of the polymkeric substance below 220 ℃ and lamination and even the molecular orientation of laying on said matrix and the enhancement layer of one deck at least of silane-crosslinked ultra-high-molecular-weight polyethylene fiber processing temperature, said enhancement layer is keeping the oriented crystalline structure of superhigh molecular weight polyethylene fibers in fact.
2, fibre reinforced polymeric shaped articles according to claim 1, it is characterized in that said molecular orientation and silane-crosslinked ultra-high-molecular-weight polyethylene fiber are under its constrained state, when scanning calorimeter measurement with differential, under the high at least 10 ℃ of temperature of original crystalline melting temperature (Tm) of the ultrahigh molecular weight polyethylene(UHMWPE) that the main fusing peak value when heating up as the second time is obtained, having at least two watery fusion peak values (Tp), is the about more than 5% of running down heat at it based on the fusing heat of the watery fusion peak value (Tp) of running down heat 50% or more and based on the summation that the high temperature side of temperature range Tm+35 ℃-Tm+120 ℃ melts the fusing heat of peak value (Tp1) simultaneously.
3, formed body according to claim 1, it is characterized in that said molecular orientation and silane-crosslinked ultra-high-molecular-weight polyethylene fiber be in the naphthalane solvent, be grafted on silane compound on the polyethylene of 135 ℃ of smallest limit viscosity [η] more than 5dl/g after spinning again, extend, follow crosslinked through the grafted silane compound, the fiber that obtains, said fiber is with Si%(weight) expression, it has 0.01-5%(weight) silane grafting amount and 0.90 above orientation degree (F).
4, formed body according to claim 2, it is characterized in that said molecular orientation and silane-crosslinked ultra-high-molecular-weight polyethylene fiber are in containing the naphthalane solvent of thinner, in the presence of radical initiator, silane compound is grafted in 135 ℃ of smallest limit viscosity [η] is spinning again after on the polyethylene more than the 5dl/g, extend, follow the fiber of the crosslinked silane compound of grafted gained.
5, formed body according to claim 1, it is characterized in that said molecular orientation and silane-crosslinked ultra-high-molecular-weight polyethylene fiber be spring rate more than 20GPa, tensile strength is the fiber of 1.2GPa.
6, formed body according to claim 1 is characterized in that said enhancement layer is by forming in the front of formed body lamination and even laying and with the molecular orientation of at least one axial orientation of formed body and long filament or the tNonwovens that is made of this long filament, fabric or the cloth of silane-crosslinked ultra-high-molecular-weight polyethylene.
7, formed body according to claim 1 is characterized in that said fiber-reinforced layer accounts for the 20-80%(volume of formed body total amount).
8, formed body according to claim 1 is characterized in that said matrix polymer is a thermoplastic resin, and its fusing point and even softening temperature are below 220 ℃.
9, formed body according to claim 7 is characterized in that said matrix polymer is the ethylene series resin.
10, formed body according to claim 1 is characterized in that said matrix polymer is the thermoset polymkeric substance, and its stiffening temperature is below 220 ℃.
11, formed body according to claim 9 is characterized in that said thermoset polymkeric substance is a Resins, epoxy.
12, formed body according to claim 1 is characterized in that said matrix polymer is that curing temperature is at the rubber below 220 ℃.
13, the making method of fiber-reinforced resin formed body, it is characterized in that the long filament of molecular orientation and crosslinked with silicane ultrahigh molecular weight (UHMW) polyethylene or the tNonwovens of forming by this long filament, weave cotton cloth or woven cloth with the configuration of the direction of face and under the restricted state in its end, make it and fusing point or softening temperature melts integrator at the thermoplastic resin below 220 ℃.
14, the making method of fiber-reinforced resin formed body, it is characterized in that the long filament of molecular orientation and silane-crosslinked ultra-high-molecular-weight polyethylene or the tNonwovens of forming by this long filament, weave cotton cloth or woven cloth with under configuration of the aspect of face and the restricted state in its end, make it to reharden with the monomer or the prepolymer integrator of stiffening temperature at the thermosetting polymer below 220 ℃.
15, the making method of fiber-reinforced rubber formed body, it is characterized in that tNonwovens that the long filament person of one-tenth with molecular orientation and silane-crosslinked ultra-high-molecular-weight polyethylene is made up of this long filament, weave cotton cloth or woven cloth with the direction configuration of face and under the restricted state in its end, make it with curing temperature at the unvulcanized rubber integrator below 220 ℃ and make it sulfuration.
Applications Claiming Priority (5)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP131396/87 | 1987-05-29 | ||
| JP62131396A JPH0784034B2 (en) | 1987-05-29 | 1987-05-29 | Fiber-reinforced resin molding and manufacturing method thereof |
| JP131397/87 | 1987-05-29 | ||
| JP62157511A JPH0717761B2 (en) | 1987-06-26 | 1987-06-26 | Fiber-reinforced rubber molding and method for producing the same |
| JP157511/87 | 1987-06-26 |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN88103280A CN88103280A (en) | 1988-12-07 |
| CN1027275C true CN1027275C (en) | 1995-01-04 |
Family
ID=26466245
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN 88103280 Expired - Fee Related CN1027275C (en) | 1987-05-29 | 1988-05-29 | Fibre reinforced polymeric shaped articles |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN1027275C (en) |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US10994510B2 (en) | 2016-12-22 | 2021-05-04 | Toray Industries, Inc. | Composite structure and method for manufacturing same |
-
1988
- 1988-05-29 CN CN 88103280 patent/CN1027275C/en not_active Expired - Fee Related
Also Published As
| Publication number | Publication date |
|---|---|
| CN88103280A (en) | 1988-12-07 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN1092689C (en) | Thermoplastic resin composition and process for production thereof | |
| CN1046460C (en) | Thermoplastic elastomer laminates and glass run channels molded therefrom | |
| CN1155628C (en) | Molded resin articles | |
| CN1155629C (en) | Unsaturated copolymers, processes for preparing same, and compositions containing the same | |
| CN100345909C (en) | Composite dispersion and process for producing the same | |
| CN101056898A (en) | Modified polyolefin-based resin for treating glass fiber, surface-treated glass fiber and fiber-reinforced polyolefin-based resin | |
| CN88102228A (en) | The linear low density polyethylene of graft modification---their preparation method | |
| CN1120857C (en) | Electrical insulating resin material, electrical insulating material, and electric wire and cable using same | |
| CN1922261A (en) | Thermoplastic elastomer composition and molded article thereof | |
| CN1285370A (en) | Application of heat-resistant rubber comosition | |
| CN1016674B (en) | Thermoplastic elastomer laminate | |
| CN1761712A (en) | Pellet comprising ethylene-alpha-olefin-non-conjugated polyene copolymer, method for producing thermoplastic elastomer and method for producing pellet comprising ethylene-alpha-olefin-non-conjugated p | |
| CN87107989A (en) | Thermoplastic elastomer composition having excellent thermal adhesiveness | |
| CN1197907C (en) | Crosslinkable rubber composition and use thereof | |
| CN87107381A (en) | Thermoplastic resin composition | |
| CN1175052C (en) | Thermoplastic resin formed article having high-rigidity and high-strength | |
| CN1184732A (en) | Soft and transparaent polyolefin resin pellet and method for mfg. same | |
| CN1031076C (en) | Molecule directed form body of ultrahigh molecular weight ethene, alpha-alkene copolymers | |
| CN1597759A (en) | Fiber-crystalline thermoplastic resin composite material and pellet thereof | |
| CN1027275C (en) | Fibre reinforced polymeric shaped articles | |
| CN1182440A (en) | Grafted polyolefinic resin and composition thereof | |
| CN1159817A (en) | Propylene resin composition for interior material for automobiles, and interior material for automobiles | |
| CN1092437A (en) | Prolylene polymer composition | |
| CN1021804C (en) | Laminated molded articles and processes for preparing same | |
| CN1033048C (en) | Molecularly oriented, silane-crosslinked ultra-high-molecular-weight polyethylene molded article and process for preparation thereof |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| C14 | Grant of patent or utility model | ||
| GR01 | Patent grant | ||
| C53 | Correction of patent for invention or patent application | ||
| COR | Change of bibliographic data |
Free format text: CORRECT: PATENTEE; FROM: MITSUI SEKIYU K.K.K. TO: MITSUI CHEMICALS, INC. |
|
| CP01 | Change in the name or title of a patent holder |
Patentee after: Mitsui Chemical Industry Co., Ltd. Patentee before: Mitsui Petrochemical Industries, Ltd. |
|
| C19 | Lapse of patent right due to non-payment of the annual fee | ||
| CF01 | Termination of patent right due to non-payment of annual fee |