Patent Application
20240117162
The invention relates to a resin-extended modified diene elastomer, to the process for manufacturing same and to rubber compositions containing same, these rubber compositions being intended in particular for the manufacture of semi-finished articles for tyres and for the manufacture of tyres.
Now that savings in fuel and the need to protect the environment have become a priority, it is desirable to produce mixtures having a hysteresis which is as low as possible in order to be able to process them in the form of rubber compositions which can be used in the manufacture of various semi-finished products participating in the manufacture of tyres, such as, for example, underlayers, sidewalls or treads, and in order to obtain tyres having a reduced rolling resistance.
Ideally, for example, a tyre tread must fulfil a great many technical requirements, which are often contradictory in nature, including good dry and wet grip while affording low rolling resistance.
One means to achieve this performance compromise is to use high-molecular-weight diene elastomers, such as for example oil-extended elastomers. However, these high-molecular-weight diene elastomers have high viscosities, and are difficult to extrude, even when an extender oil is added to them. Non-homogeneous extrusion produces poor-quality extrudates which do not meet the dimensional tolerances required by the factory processes for the manufacture of semi-finished articles for tyres. To remedy this problem, it is possible to reduce the viscosity of these oil-extended elastomers by prolonging the mixing time, in particular before extrusion. However, these actions are undesirable because they can cause degradation of these elastomers and hence degrade the mechanical properties of the resulting crosslinked rubber compositions. In addition, an increase in the mixing time incurs cost in the industrial manufacturing process.
Another means for achieving the performance compromise of dry and wet grip while affording low rolling resistance consists in using a high content of plasticizing resins in the low-hysteresis rubber compositions. However, this use of a high content of plasticizing resins has the consequence of increasing the tackiness of the composition. This increase in the tackiness of the composition is detrimental to the processability of the rubber composition in the various mixing devices.
To overcome this drawback, the Applicant has developed resin-extended diene elastomers. Such diene elastomers are described in application WO2019/020948.
Continuing its research, the Applicant sought to further improve the processability of the resin-extended diene elastomers by yet further reducing the tackiness of the rubber compositions containing them without degrading the other properties of these compositions.
The aim of the present invention is therefore to provide resin-extended diene elastomers which make it possible to obtain rubber compositions having improved processability while retaining good hysteresis properties or even improving these properties. These improvements should also not come at the expense of the quality of the extrudate.
This aim is achieved by specific resin-extended diene elastomers and by rubber compositions containing them. More precisely, this object is achieved via the selection of a resin-extended modified diene elastomer based on a plasticizing resin and a diene elastomer based on a plasticizing resin and a diene elastomer having a number-average molar mass before modification Mn1 and a number-average molar mass Mn2 after modification, Mn1 and Mn2 being measured by triple detection size exclusion chromatography as described below; the modified diene elastomer comprises branched chains and corresponds to the following general formula (I)
in which:
This modified diene elastomer as defined above advantageously confers on the rubber compositions containing it a significantly reduced tackiness compared to the resin-extended diene elastomers of the prior art (and thus an improved processability) and an improvement in the hysteresis properties corroborating an improvement in the rolling resistance performance for the tyres. In addition, the modified diene elastomer as defined above has the advantage of providing a rubber composition of homogeneous and uniform quality, which is reflected during extrusion thereof by a good finish of the extrudate, both at the level of its surface and of its edges.
Another subject of the present invention relates to a rubber composition based on at least one resin-extended modified diene elastomer as defined above, at least one reinforcing filler and at least one crosslinking system. These compositions have the following advantages: they experience little to no adhesion to mixing devices and other tools for manufacturing compositions and semi-finished articles for tyres, they have good hysteresis properties and the extrusion thereof is reproducible and homogeneous.
Another subject of the present invention relates to a semi-finished rubber article for a tyre comprising at least one crosslinkable or crosslinked rubber composition as defined above. Preferably, the semi-finished article for a tyre is a tread.
Another subject of the present invention is a tyre comprising at least one rubber composition as defined above or a semi-finished article defined above.
Measurements and tests used Measurement of the Mn, Mw and PDI of the elastomers by triple detection size exclusion chromatography (SEC-3D)
The number-average molar mass (Mn), and where appropriate the weight-average molar mass (Mw) and the polydispersity index (PDI) of the elastomers are determined in an absolute manner, by triple detection size exclusion chromatography “SEC-3D” (SEC: Size Exclusion Chromatography).
Triple detection size exclusion chromatography has the advantage of measuring average molar masses directly without calibration.
The refractive index increment do/dc of the sample is first determined. For this, the sample is dissolved beforehand in tetrahydrofuran at different precisely known concentrations (0.5 g/l, 0.7 g/l, 0.8 g/l, 1 g/l and 1.5 g/l) and then each solution is filtered through a filter with a porosity of 0.45 μm. Each solution is subsequently directly injected, using a syringe driver, into a Wyatt differential refractometer of Optilab T-Rex trade name of wavelength 658 nm and thermostatically controlled at 35° C. The refractive index is measured by the refractometer at each concentration. The Astra software from Wyatt produces a straight line of the signal of the detector as a function of the concentration of the sample. The Astra software automatically determines the slope of the straight line corresponding to the refractive index increment of the sample in the tetrahydrofuran at 35° C. and at the wavelength of 658 nm.
In order to determine the average molar masses, use is made of the 1 g/l solution previously prepared and filtered, which is injected into the chromatographic system. The apparatus used is a Waters Alliance chromatographic line. The elution solvent is tetrahydrofuran protected from oxidation with 250 ppm of BHT (2,6-di(tert-butyl)-4-hydroxytoluene), the flow rate is 1 ml·min−1, the temperature of the system is 35° C. and the analytical time is 60 min. The columns used are a set of three Agilent columns of PL Gel Mixed B LS trade name. The volume of the sample solution injected is 100 μl. The detection system is composed of a Wyatt differential viscometer of Viscostar II trade name, of a Wyatt differential refractometer of Optilab T-Rex trade name of wavelength 658 nm and of a Wyatt multi-angle static light scattering detector of wavelength 658 nm and of Dawn Heleos 8+ trade name.
For the calculation of the number-average molar masses and the polydispersity index, the value of the refractive index increment do/dc of the solution of the sample obtained above is integrated. The software for processing the chromatographic data is the Astra system from Wyatt.
Measurement of the Mn, Mw and PDI of the plasticizing polymers by refractive index size exclusion chromatography (SEC-RI)
The SEC (Size Exclusion Chromatography) technique makes it possible to separate macromolecules in solution according to their size through columns filled with a porous gel. The macromolecules are separated according to their hydrodynamic volume, the bulkiest being eluted first.
Without being an absolute method, SEC makes it possible to comprehend the distribution of the molar masses of a plasticizing polymer (oil or resin). The various number-average molar masses (Mn) and weight-average molar masses (Mw) can be determined from commercial standards and the polydispersity index (PDI=Mw/Mn) can be calculated via a “Moore” calibration.
There is no specific treatment of the plasticizing polymer sample before analysis.
The latter is simply dissolved in the elution solvent at a concentration of approximately 1 g·l−1. The solution is then filtered through a filter with a porosity of 0.45 μm before injection.
The apparatus used is a Waters Alliance chromatographic line. The elution solvent is either tetrahydrofuran protected from oxidation with 250 ppm of BHT (butylated hydroxytoluene), or tetrahydrofuran without antioxidant, the flow rate is 1 ml·min−1, the temperature of the system is 35° C. and the analytical time is 45 min. The columns used are either a set of three Agilent columns of Polypore trade name or a set of four Agilent columns: two of PL Gel Mixed D trade name and two of PL Gel Mixed E trade name. The volume of the solution of the plasticizing polymer sample injected is 100 μl. The detector is a Waters 2410 differential refractometer and the software for processing the chromatographic data is the Waters Empower system.
The calculated average molar masses are relative to a calibration curve produced with polystyrene standards.
Differential Calorimetry
The glass transition temperatures (Tg) of the elastomers, of the resins and of the plasticizing oils are determined using a differential scanning calorimeter according to the standard ASTM D3418-08 (2008).
Near-infrared (NIR) spectroscopy
The microstructure of the elastomers is characterized by the near-infrared (NIR) spectroscopy technique.
Near-infrared (NIR) spectroscopy is used to quantitatively determine the content by mass of styrene in the elastomer and also its microstructure (relative distribution of the 1,2-, trans-1,4- and cis-1,4-butadiene units). The principle of the method is based on the Beer-Lambert law generalized for a multicomponent system. As the method is indirect, it involves a multivariate calibration [Vilmin, F., Dussap, C. and Coste, N., Applied Spectroscopy, 2006, 60, 619-29] carried out using standard elastomers having a composition determined by 13C NMR. The styrene content and the microstructure are then calculated from the NIR spectrum of an elastomer film approximately 730 μm in thickness. The spectrum is acquired in transmission mode between 4000 and 6200 cm−1 with a resolution of 2 cm−1 using a Bruker Tensor 37 Fourier-transform near-infrared spectrometer equipped with an InGaAs detector cooled by the Peltier effect.
Inherent Viscosity
The inherent viscosity of the elastomers at 25° C. is determined from a 0.1 g·dl−1 solution of elastomer in toluene, according to the following principle:
The inherent viscosity is determined by the measurement of the flow time t of the polymer solution and of the flow time t0 of the toluene in a capillary tube.
The flow time of the toluene and the flow time of the 0.1 g·dl−1 polymer solution are measured in an Ubbelohde tube (diameter of the capillary 0.46 mm, capacity from 18 to 22 ml) placed in a bath thermostatically controlled at 25±0.1° C.
The inherent viscosity is obtained by the following relationship:
where:
Dynamic Properties
The dynamic properties and in particular tan δ max are measured on a viscosity analyser (Metravib VA4000) according to the standard ASTM D 5992-96. The response is recorded of a sample of vulcanized composition (cylindrical test specimen with a thickness of 2 mm and a cross section of 79 mm2), subjected to a simple alternating sinusoidal shear stress, at a frequency of 10 Hz, under standard temperature conditions (23° C.) according to the standard ASTM D 1349-99. A strain amplitude sweep is carried out from 0.1% to 50% peak-to-peak (outward cycle) and then from 50% to 0.1% peak-to-peak (return cycle). The result more particularly made use of is the loss factor tan S. For the return cycle, the maximum value of tan δ observed, denoted tan δ max, is indicated. This value is representative of the hysteresis of the material and in the present case of the rolling resistance: the smaller the value of tan δ max, the lower the rolling resistance. In the examples, the results of the dynamic properties are given in base 100. An index of less than 100 will indicate an improvement in the hysteresis properties, and thus an improvement in the rolling resistance performance of a tyre.
Measurement of the Tack of the Compositions
The tack of the rubber compositions is measured by means of a tack measurement, which is also referred to as an adhesion test, also known as a probe-tack or micro-tack test. This test corresponds to a test of contact between a surface (a probe) and an adhesive (the composition).
The test is performed at a temperature of 70° C. corresponding to the temperature of the rubber composition and of the surface; the composition not being vulcanized. The variation in the force applied as a function of the movement is recorded. The test is carried out in accordance with the requirements of the standard ASTM D2979-01 (2009) under the following conditions:
The tack index is calculated in base 100 with respect to the control with the peeling energy at 70° C. In this way, a result of less than 100 indicates a decrease in tackiness which corroborates a better processability of the composition.
Measuring the Garvey Rating of the Extruded Compositions
The determination of the Garvey rating representing the extrudability of the raw (that is to say non-vulcanized) compositions is performed in accordance with the standard ASTM D2230-96 (2002).
The appearance of the extrudate is rated according to the B system, namely a surface rating ranging from E to A, the letter E being the worst rating, and an edge rating ranging from 1 to 10 in ascending order, the number 1 being the lowest rating.
Determination of the amount of plasticizing resin in the resin-extended elastomer.
The determination of the amount of plasticizing resin in the resin-extended elastomer is also performed by refractive index size exclusion chromatography (SEC-RI) analysis.
There is no specific treatment of the resin-extended elastomer sample before analysis. It is simply dissolved to a concentration of about 1 g/l, in tetrahydrofuran with the antioxidant BHT at 250 ppm. The solution is then filtered through a filter with a porosity of 0.45 μm before injection.
The apparatus used is a Waters Alliance 2695 chromatograph. The elution solvent is tetrahydrofuran with the antioxidant BHT at 250 ppm. The flow rate is 1 ml/min, the temperature of the system is 35° C. and the analysis time is 35 min.
Use is made of a set of 3 Agilent columns in series, of PL Gel Mixed-D and PL Gel Mixed-E trade names. This set is composed of 2 Agilent PL Gel Mixed D columns and one Agilent PL Gel Mixed E column in series.
The volume of the solution of the resin-extended elastomer sample injected is 100 μl.
The detector is a Waters 2410 differential refractometer, of wavelength 810 nm, and the software for processing the chromatographic data is the Waters Empower system.
Calibrants using a non-resin-extended elastomer of the same microstructure as the resin-extended elastomer are used. These calibrants are prepared in tetrahydrofuran with the antioxidant BHT at 250 ppm (BHT butylated hydroxytoluene). Several calibrants are prepared from a non-resin-extended elastomer at precisely known concentrations in g/l so as to obtain a calibration range. Each calibrant is injected to 100 μl into the chromatographic system. With the aid of the data reprocessing software, each calibrant peak is integrated. It is then possible to determine the total area of the peak of each calibrant. A calibration straight line is then constructed by plotting the area of the peak of the calibrant as a function of the concentration.
The resin-extended elastomer is then injected following the creation of the calibration straight line. Since the signals for the resin and the elastomer are separated by means of the SEC columns, a quantification can thus be performed. The peak obtained for the elastomer is then integrated using the data reprocessing software; the area for said peak is then reported on the previously constructed calibration straight line. It is then possible to deduce the elastomer concentration in g/L in the resin-extended elastomer (Celasto). The concentration of the dissolved resin-extended elastomer is known (Csamp). Quantification of the resin content is thus performed indirectly via the following relationship:
Resin content=1−Celasto/Csamp
In the present description, unless expressly indicated otherwise, all the percentages (%) shown are percentages (%) by mass.
Moreover, any interval of values denoted by the expression “between a and b” represents the range of values extending from more than a to less than b (that is to say, limits a and b excluded), whereas any interval of values denoted by the expression “from a to b” means the range of values extending from a up to b (that is to say, including the strict limits a and b).
For the purposes of the present invention, the expression “part by weight per hundred parts by weight of elastomer” (or phr) should be understood as meaning the part by mass per hundred parts by mass of elastomer.
In the present description, the term “predominantly” or “predominant”, in connection with a compound, means that this compound is predominant among the compounds of the same type in the composition, i.e. that it is the one which represents the largest amount by mass among the compounds of the same type. In the same way, a “predominant” species in a modified elastomer is that representing the largest fraction by weight among the species constituting the modified diene elastomer, relative to the total weight of the modified diene elastomer. In a system comprising just one compound of a certain type, the latter is predominant for the purposes of the present invention. Preferably, the term predominant is understood to mean a compound present at more than 50%, more preferentially still a compound present at more than 60% by weight.
In the present description, when no further information is given, primary or secondary amine is understood to mean a primary or secondary amine which is or is not protected by a protective group known to a person skilled in the art.
In the present description, modified diene elastomer is understood to mean a mixture of macromolecules resulting from the reaction of a living diene elastomer with a modifying agent comprising at least two functions which are reactive with respect to the reactive end of the living diene elastomer.
A person skilled in the art will understand that a modification reaction with a modifying agent comprising more than one function reactive with respect to the living elastomer results in a mixture of macromolecules modified at the chain ends and of macromolecules coupled or star-branched to at least three branches and at most as many branches as reactive functions borne by the modifying agent; the coupled and star-branched forms constituting the branched chains of the modified elastomer. Depending on the operating conditions, mainly the molar ratio of the modifying agent to the living chains and the number of its reactive functions, certain species are more or less present, indeed even predominant, in the mixture.
In the present description, the expression “monomer unit”, whether it be diene or other, is understood to be a repeat unit of the polymer resulting from the monomer in question.
In the present description, the expression “branching unit” is understood as a non-repeating unit (there is just one of them in the polymer), resulting from the modifying agent with which the living diene elastomer chains has or have reacted and to which the diene elastomer chains are attached. The branching unit may consist, for example, of an atom to which the diene elastomer chains are attached, it being possible for this atom to be unsubstituted or substituted by chemical functions and/or groups.
The compounds mentioned in the description may be of fossil origin or may be biobased. In the latter case, they may be partially or completely derived from biomass or may be obtained from renewable starting materials derived from biomass. Similarly, the compounds mentioned may also originate from the recycling of already-used materials, i.e. they may be partially or totally derived from a recycling process, or obtained from starting materials which are themselves derived from a recycling process. Polymers, plasticizers, fillers, etc. are concerned in particular.
For the purposes of the present invention, the term “resin-extended elastomer” is understood to mean a solid material of composite type formed from an elastomer and a resin which are intimately mixed with one another; the mixing of the resin with the elastomer being carried out in a liquid medium in an organic solvent, preferably in a non-polar organic solvent. The mixing of the resin is therefore carried out in an elastomer in solution; that is to say the organic solvent and said elastomer form just a single phase visible to the naked eye. There is no precipitate or suspension of particles of said elastomer in the solution. This definition therefore excludes materials which would have been obtained by bulk mixing (or dry-mixing) an elastomer with a resin. Given that the two constituents of this material are intimately mixed with one another in liquid phase, a single Tg value is obtained when this parameter is measured for the resin-extended elastomer. This Tg of the resin-extended elastomer is different from that of the synthetic elastomer and from that of the plasticizing resin measured before they are mixed.
A first subject of the present invention relates to a resin-extended modified diene elastomer based on a plasticizing resin and a diene elastomer having a number-average molar mass before modification Mn1 and a number-average molar mass Mn2 after modification, Mn1 and Mn2 being measured by triple detection size exclusion chromatography as described above; the modified diene elastomer comprises branched chains and corresponds to the following general formula (I)
in which:
the modified diene elastomer has an Mn2 of greater than or equal to 200 000 g/mol and an Mn2/Mn1 ratio of strictly greater than 1.00.
The resin-extended modified diene elastomer based on a plasticizing resin and a diene elastomer according to the invention comprises at least one modified diene elastomer and at least one plasticizing resin. This resin-extended modified diene elastomer can also contain other extenders such as, for example, extender oils, in particular extender oils of petroleum or natural origin, such as, for example, oils comprising triglycerides. When the resin-extended modified diene elastomer also comprises an extender oil, the content of the latter is preferentially lower than the content of the resin in the modified diene elastomer. Preferentially, the resin-extended modified diene elastomer according to the invention consists, preferentially essentially, of a modified diene elastomer as defined below and at least one plasticizing resin; that is to say it does not comprise any extender oil.
By virtue of the characteristics presented above, it is possible to obtain a modified diene elastomer imparting a better processability on the composition containing it, while also retaining or even improving the hysteresis properties and retaining a good quality of the extrudate.
Those skilled in the art will readily understand that when the Mn2/Mn1 ratio of a diene elastomer is equal to 1.00, this diene elastomer is not modified within the meaning of the present invention; that is to say that it is predominantly, or preferentially exclusively, linear. It may however be functionalized at the chain end or at the chain extremity, but this functionalization is not a branching unit for the purposes of the present invention.
Preferentially, the Mn2/Mn1 ratio is greater than or equal to 1.10, more preferentially greater than or equal to 1.20; and preferably is within a range extending from 1.30 to 4.00; more preferentially within a range extending from 1.40 to 2.00.
Preferentially, the number-average molar mass Mn1 is greater than or equal to 140 000 g/mol, preferably is within a range extending from 150 000 g/mol to 230 000 g/mol, and in particular the resin-extended modified diene elastomer has an Mn2/Mn1 ratio of strictly greater than 1.10; more preferentially extending within a range of from 1.30 to 4.00; more preferentially still in a range extending from 1.40 to 2.00.
Preferentially, the resin-extended modified diene elastomer according to the invention has a number-average molar mass Mn2 which is greater than or equal to 205 000 g/mol, preferably greater than or equal to 210 000 g/mol, more preferentially still greater than or equal to 250 000 g/mol, more preferentially still greater than 300 000 g/mol.
Preferentially, the resin-extended modified diene elastomer according to the invention has a number-average molar mass Mn2 which is greater than or equal to 205 000 g/mol, preferably greater than or equal to 210 000 g/mol, more preferentially still greater than or equal to 250 000 g/mol, more preferentially still greater than 300 000 g/mol and has an Mn2/Mn1 ratio of greater than or equal to 1.10, more preferentially greater than or equal to 1.20; preferably within a range extending from 1.30 to 4.00; more preferentially in a range extending from 1.40 to 2.00.
Elastomer capable of being used within the context of the invention should be understood in a known way as meaning a synthetic elastomer consisting at least in part of conjugated or non-conjugated diene monomer units.
Synthetic diene elastomer is understood more particularly to mean:
In the case of copolymers with one or more vinylaromatic monomers, the latter can contain from 20% to 99% by weight of conjugated diene units and from 1% to 80% by weight of units resulting from vinylaromatic monomers.
The following are suitable in particular as conjugated diene monomers having from 4 to 12 carbon atoms: 1,3-butadiene, 2-methyl-1,3-butadiene (isoprene), 2,3-di (C1-C5 alkyl)-1,3-butadienes such as for example 2,3-dimethyl-1,3-butadiene, 2,3-diethyl-1,3-butadiene, 2-methyl-3-ethyl-1,3-butadiene, 2-methyl-3-isopropyl-1,3-butadiene, an aryl-1,3-butadiene, 1,3-pentadiene, 2,4-hexadiene and mixtures of these monomers. Preferably, the conjugated diene monomer having from 4 to 12 carbon atoms is 1,3-butadiene or 2-methyl-1,3-butadiene, and more preferentially is 1,3-butadiene.
The following, for example, are suitable as vinylaromatic monomers: styrene, ortho-, meta- or para-methylstyrene, the “vinyltoluene” commercial mixture, para-(tert-butyl)styrene, methoxystyrenes, chlorostyrenes, vinylmesitylene, divinylbenzene or vinylnaphthalene, and a mixture of these monomers. Preferably, the vinylaromatic monomer is styrene.
Preferentially, the modified diene elastomer is selected from the group consisting of polybutadienes, synthetic polyisoprenes, butadiene copolymers, isoprene copolymers and the mixtures of these elastomers.
Preferentially, the modified diene elastomer is selected from the group consisting of polybutadienes (BRs), synthetic polyisoprenes (IRs), copolymers of butadiene and styrene (SBRs), copolymers of isoprene and styrene (SIRs), copolymers of isoprene and butadiene (BIRs), and isoprene/butadiene/styrene copolymers (SBIRs).
More preferentially still, the modified diene elastomer is selected from the group consisting of polybutadienes and copolymers of butadiene and styrene.
More preferentially still, the modified diene elastomer is a copolymer of styrene and butadiene.
The diene elastomers can have any microstructure, which depends on the polymerization conditions used. The diene elastomers can be block, random, sequential, or microsequential elastomers. Preferentially, the diene elastomer is a random diene elastomer.
Preferentially, the modified diene elastomer may have any Tg within a range extending from 1° C. to −68° C., the Tg being measured in accordance with the standard described above and on the modified diene elastomer before its extension with the resin.
Preferentially suitable are polybutadienes and in particular those having a 1,2-unit content (also called vinyl %) within a range extending from 30 to 70, more preferentially ranging from 40% to 60% by weight, relative to the weight of the polybutadiene.
Preferentially suitable are copolymers of styrene and butadiene and in particular those having a styrene content within a range extending from 1% to 50% by weight relative to the total weight of the copolymer, and a content of 1,2-bonds of the butadiene part within a range extending from 20% to 50% by weight relative to the weight of the butadiene part, and a content of trans-1,4-bonds within a range extending from 15% to 80% by weight relative to the weight of the butadiene part.
The resin-extended modified diene elastomer according to the invention is a synthetic diene elastomer comprising at least two diene elastomer branches connected to a core which can be an atom or a group of atoms. Linear and comb diene elastomers are not modified diene elastomers for the purposes of the present invention.
Thus, according to the invention, the modified diene elastomer comprises branched macromolecules comprising within their structure an n-functional branching unit, n being equal to 2, 3 or 4, consisting of an atom selected from the group consisting of a phosphorus atom, a silicon atom, a tin atom, said atom being substituted by at least two diene elastomer branches and at most n diene elastomer branches. Those skilled in the art will readily understand that the number of elastomer branches cannot be greater than the valence of the atom constituting the branching unit. Those skilled in the art will understand that the linear species of the modified diene elastomer are minority species.
More precisely, the resin-extended modified diene elastomer according to the invention comprises branched chains and corresponds to the following general formula (I)
in which:
According to a variant of the invention, in formula (I), E can represent a branch of a butadiene homopolymer or a butadiene copolymer; preferably E can represent a branch of a polybutadiene or of a copolymer of styrene and butadiene, more preferentially still a copolymer of styrene and butadiene.
The expression “Ci-Cj alkyl” is understood to mean a linear, branched or cyclic hydrocarbon group comprising from i to j carbon atoms; i and j being integers.
The expression “Ci-Cj aryl” is understood for the purposes of the present invention to mean one or more aromatic rings having from i to j carbon atoms, these possibly being joined or fused. In particular, the aryl groups can be monocyclic or bicyclic groups, preferably monocyclic groups. By way of example, an aryl can be phenyl. In the context of the present invention, the aryl groups can be substituted by one or more identical or different substituents. Among the substituents of the aryl groups, mention may be made, by way of example, of alkyl groups (as defined above).
The expression “Ci-Cj alkanediyl” is understood to mean, for the purposes of the present invention, a divalent group of general formula CnH2n, derived from an alkane having between i and j carbon atoms. The divalent group may be linear or branched and optionally be substituted.
According to a variant of the invention, in formula (I), R1, independently at each occurrence, can represent a C1-C8 alkyl or a C6-C12 aryl, more preferentially a C1-C4 alkyl or a C6 aryl. More preferentially still, R1, independently at each occurrence, can represent a methyl, an ethyl or a phenyl that is unsubstituted or substituted by one or more C1-C4 alkyls. More preferentially still, R1, independently at each occurrence, can represent a methyl, an ethyl or a phenyl that is unsubstituted or substituted by one or more t-butyl groups.
According to a variant of the invention, in formula (I), R2, independently at each occurrence, can represent a methyl, an ethyl or a propyl.
According to a variant of the invention, in formula (I), R3 can be a C1-C10 alkanediyl, preferably a C1-C6 alkanediyl, more preferentially still propanediyl.
According to a variant of the invention, in formula (I), the function capable of interacting with a reinforcing filler can comprise at least one heteroatom selected from nitrogen, sulfur, oxygen and phosphorus.
Preferentially in a variant of the invention, in formula (I), the function capable of interacting with the reinforcing filler can be a primary, secondary or tertiary amine function, isocyanates, imines, cyanos, thiols, carboxylates, epoxides or primary, secondary or tertiary phosphines.
Mention may thus be made, as secondary or tertiary amine function, of amines substituted by C1-C10 alkyl, preferably C1-C4 alkyl, radicals, more preferentially a methyl or ethyl radical, or else of cyclic amines forming a heterocycle containing a nitrogen atom and at least one carbon atom, preferably from 2 to 6 carbon atoms. Suitable, for example, are the methylamino-, dimethylamino-, ethylamino-, diethylamino-, propylamino-, dipropylamino-, butylamino-, dibutylamino-, pentylamino-, dipentylamino-, hexylamino-, dihexylamino- or hexamethyleneamino-groups, preferably the diethylamino- and dimethylamino-groups.
Mention may be made, as imine function, of ketimines. Suitable, for example, are the (1,3-dimethylbutylidene)amino-, (ethylidene)amino-, (1-methylpropylidene)amino-, (4-N,N-dimethylaminobenzylidene)amino-, (cyclohexylidene)amino-, dihydroimidazole and imidazole groups.
Mention may thus be made, as carboxylate function, of acrylates or methacrylates. Such a function is preferably a methacrylate.
Mention may be made, as epoxide function, of the epoxy or glycidyloxy groups.
Mention may be made, as secondary or tertiary phosphine function, of phosphines substituted by C1-C10 alkyl, preferably C1-C4 alkyl, radicals, more preferentially a methyl or ethyl radical, or else diphenylphosphine. Suitable, for example, are the methylphosphino-, dimethylphosphino-, ethylphosphino-, diethylphosphino, ethylmethylphosphino- and diphenylphosphino-groups.
More preferentially still, the preferred resin-extended modified diene elastomer of formula (II) can be the one in which:
According to a variant of the invention, among the elastomers of formula (I), preference is given to those where q is equal to 1.
More preferentially in this variant where q=1, the elastomers of formula (I) can be those for which: E represents a branch of a butadiene homopolymer or of a butadiene copolymer; preferably a branch of a polybutadiene or of a copolymer of styrene and butadiene; Z represents a silicon atom; R1 represents, independently at each occurrence, a C1-C10 alkyl; R2 represents, independently at each occurrence, a C1-C10 alkyl, preferably C1-C4 alkyl; R3 represents a C1-C10 alkanediyl; Y is a hydrogen atom or a function capable of interacting with a reinforcing filler; m is an integer being equal to 2, 3 or 4; n is an integer being equal to 0, 1 or 2; p is an integer being equal to 0, 1 or 2 and m+n+p+q=4.
According to another variant of the invention, among the elastomers of formula (I), preference is given to those where q=0.
More preferentially in this variant where q=0, the elastomers of formula (I) can be those for which: E represents a branch of a butadiene homopolymer or of a butadiene copolymer; preferably a branch of a polybutadiene or of a copolymer of styrene and butadiene; Z represents a phosphorus atom; R1, independently at each occurrence, represents a C1-C10 alkyl or a C6 aryl; R2 represents, independently at each occurrence, a C1-C10 alkyl, preferably C1-C4 alkyl; m is an integer being equal to 2 or 3; n is an integer being equal to 0, 1 or 2; p is an integer being equal to 0 or 1 and m+n+p=3.
Description of the Resin
The second constituent of the resin-extended modified diene elastomer in accordance with the invention is a plasticizing resin.
As is known to those skilled in the art, the term “resin” is reserved in the present patent application, by definition, for a compound which is solid at ambient temperature (23° C., 1 atm), as opposed to a plasticizer that is liquid at ambient temperature such as an oil.
Plasticizing resins are polymers that are well known to those skilled in the art. These are hydrocarbon resins essentially based on carbon and hydrogen, but which may include other types of atoms, which can be used in particular as plasticizing agents or tackifying agents in polymer matrices. They are by nature miscible (i.e. compatible) at the contents used with the compositions of diene elastomer(s) for which they are intended, so as to act as true diluents. They have been described, for example, in the work entitled “Hydrocarbon Resins” by R. Mildenberg, M. Zander and G. Collin (New York, VCH, 1997, ISBN 3-527-28617-9), Chapter of which is devoted to their applications, in particular in the tyre rubber field (5.5. “Rubber Tires and Mechanical Goods”). They can be aliphatic, cycloaliphatic, aromatic, hydrogenated aromatic, or of the aliphatic/aromatic type, that is to say based on aliphatic and/or aromatic monomers. They can be natural or synthetic and may or may not be petroleum-based (if such is the case, they are also known under the name of petroleum resins). They are preferentially exclusively hydrocarbon-based, i.e. they include only carbon and hydrogen atoms. Their Tg is preferably greater than or equal to 0° C., preferably greater than or equal to 20° C. (usually in a range extending from 30° C. to 95° C.). In the present patent application, the terms “plasticizing resins”, “hydrocarbon resins” and “plasticizing hydrocarbon resins” are interchangeable. The Tg of the resins that can be used within the context of the present invention is measured in accordance with the standard ASTM D3418-08 (2008).
As is known, these plasticizing resins can also be described as thermoplastic resins in the sense that they soften when heated and can thus be moulded. They can also be defined by a softening point or temperature. The softening point of a plasticizing resin is generally approximately 50° C. to 60° C. higher than its Tg value. The softening point is measured in accordance with the standard ISO 4625 of 2012 (ring and ball method).
Preferentially, the plasticizing resin that can be used within the context of the present invention has a Tg of greater than or equal to 0° C., preferably greater than or equal to 20° C., preferably greater than or equal to 30° C. (in particular between 30° C. and 95° C.). It is understood that the Tg of the plasticizing resin included in the formulation of the resin-extended modified diene elastomer in accordance with the invention is measured on the plasticizing resin prior to mixing it with the modified diene elastomer.
Preferentially, the plasticizing resin that can be used within the context of the present invention has a softening point of greater than or equal to 50° C. (in particular of between 50° C. and 150° C.) measured in accordance with the standard ISO 4625 of 2012 (ring and ball method).
Preferentially, the plasticizing resin that can be used in the context of the present invention has a number-average molar mass (Mn) of between 400 and 2000 g/mol, preferentially between 500 and 1500 g/mol.
Preferentially, the plasticizing resin that can be used within the context of the present invention has a polydispersity index (PDI) of less than 3 (reminder: PDI=Mw/Mn with Mw the weight-average molar mass). The Mn, the Mw and the PDI of the plasticizing resins are measured according to the refractive index size exclusion chromatography method as described above.
More preferentially, the plasticizing resin that can be used within the context of the present invention has a Tg of greater than or equal to 20° C., preferably greater than or equal to 30° C., and an Mn of between 400 and 2000 g/mol, preferentially between 500 and 1500 g/mol.
More preferentially, the plasticizing resins that can be used within the context of the present invention can have all of the preferential characteristics above.
Preferentially, the plasticizing resin that can be used within the context of the present invention is selected from the group consisting of aliphatic resins, aromatic resins and mixtures of these resins.
As examples of such plasticizing resins that can be used within the context of the present invention, mention may be made of those selected from the group consisting of cyclopentadiene (abbreviated as CPD) homopolymer or copolymer resins, dicyclopentadiene (abbreviated as DCPD) homopolymer or copolymer resins, terpene homopolymer or copolymer resins, C5 cut homopolymer or copolymer resins, C9 cut homopolymer or copolymer resins, mixtures of C5 cut homopolymer or copolymer resins and of C9 cut homopolymer or copolymer resins, α-methylstyrene homopolymer or copolymer resins, and mixtures of these resins.
All of the above plasticizing resins are well known to those skilled in the art and are commercially available, for example sold by Exxon Mobil under the name Escorez as regards C5 cut/styrene resins or C5 cut resins or C9 cut resins and CPD or DCPD resins.
Preferentially, the content of plasticizing resin in the resin-extended elastomer is in a range extending from 5 to 100 phr, preferably from 30 to 80 phr. The content of plasticizing resin in the resin-extended modified diene elastomers was measured according to the method described above.
Process for manufacturing the resin-extended modified diene elastomer
The modified diene elastomer of formula (I) according to the invention can be obtained by any process in which the resin is added to the modified diene elastomer in solution in an organic solvent, preferably in a nonpolar solvent.
According to a first embodiment of the process for manufacturing the resin-extended modified diene elastomer of the invention, an organic solvent, preferably an organic non-polar solvent, is brought into contact with a modified diene elastomer comprising branched chains corresponding to the formula (I) as defined above and having a number-average molar mass before modification Mn1 and a number-average molar mass Mn2 after modification, Mn1 and Mn2 being measured by triple detection size exclusion chromatography as described above such that Mn2 is greater than or equal to 200 000 g/mol and that the Mn2/Mn1 ratio is strictly greater than 1.00, to obtain a solution of modified diene elastomer of formula (I). At least one plasticizing resin as defined above is then added to the solution obtained previously. This resin can be added directly into the solution of modified diene elastomer comprising branched chains corresponding to the formula (I), that is to say by adding this resin in solid form, or the resin in solid form can be dissolved beforehand in an organic solvent, preferably in the same organic solvent as that used in the preceding step. In another variant, the resin can be heated to a temperature greater than its softening point and be incorporated into the solution containing the modified diene elastomer in molten form. After homogenization of the organic solvent solution comprising the modified diene elastomer comprising branched chains corresponding to formula (I) and the plasticizing resin, the solvent is removed by any means known to those skilled in the art, such as, for example, steam stripping. The resin-extended modified diene elastomer is recovered in the form of “crumb” which can be washed and dried, and possibly shaped in the form of rubber balls in particular for their storage and their later use.
According to a second embodiment of the process for manufacturing the resin-extended modified diene elastomer according to the invention, at least the following steps are carried out:
Z(R2)p(T)r(R3-Y)q (II)
in which:
The term “halogen” denotes an atom selected from the group formed of fluorine (F), chlorine (Cl), bromine (Br), iodine (I). Preferably, in formula (II), the halogen is chlorine.
Preferably, in formula (II), R4, independently at each occurrence, can represent a C1-C8 alkyl or a C6-C12 aryl, more preferentially a C1-C4 alkyl or a C6 aryl. More preferentially still, R4, independently at each occurrence, can represent a methyl, an ethyl or a phenyl that is unsubstituted or substituted by one or more C1-C6 alkyls. More preferentially still, R4, independently at each occurrence, can represent a methyl, an ethyl or a phenyl that is unsubstituted or substituted by one or more t-butyl groups.
Preferably, in formula (II), R2, independently at each occurrence, can represent a methyl, an ethyl or a propyl.
Preferably, in formula (II), R3 can be a C1-C10 alkanediyl, more preferentially still a C1-C6 alkanediyl, and more so propanediyl.
Preferably, in formula (II), the function capable of interacting with the reinforcing filler can comprise at least one heteroatom selected from nitrogen, sulfur, oxygen and phosphorus.
Preferably, in formula (II), the function capable of interacting with the reinforcing filler can be a primary, secondary or tertiary amine function, isocyanates, imines, cyanos, thiols, carboxylates, epoxides or primary, secondary or tertiary phosphines.
Preferably, in formula (II), the function capable of interacting with a reinforcing filler can preferentially be a protected or unprotected primary amine, a protected or unprotected secondary amine or a tertiary amine. The nitrogen atom can then be substituted by two identical or different groups which can be a trialkylsilyl radical, the alkyl group having 1 to 4 carbon atoms, or a C1-C10 alkyl, preferably C1-C4 alkyl, radical, more preferentially a methyl or ethyl radical, or else the two substituents of the nitrogen form, with the latter, a heterocycle containing a nitrogen atom and at least one carbon atom, preferably from 2 to 6 carbon atoms.
More preferentially still, the preferred agent of formula (II) can have the following characteristics:
According to a variant, among the modifying agents of formula (II), preference is given to those of formula (I) where q is equal to 1.
Preferentially, in this variant where q=1, the modifying agents of formula (II) that are even more preferred can be those for which: Z represents a silicon atom; T represents a halogen atom or an OR4 radical with R4 a C1-C10 alkyl; R2 represents, independently at each occurrence, a C1-C10 alkyl, preferably C1-C4 alkyl; R3 represents a C1-C10 alkanediyl; Y is a hydrogen atom or a function capable of interacting with a reinforcing filler; p represents an integer equal to 0, 1 or 2; r represents an integer equal to 2, 3 or 4; and r+p+q=4.
According to another variant, among the modifying agents of formula (II), preference is given to those of formula (I) where q is equal to 0.
Preferentially, in this variant where q=0, the modifying agents of formula (II) that are even more preferred can be those for which: Z represents a phosphorus atom; T represents a halogen atom or an OR4 radical with R4 a C1-C10 alkyl or a C6 aryl; R2 represents, independently at each occurrence, a C1-C10 alkyl, preferably C1-C4 alkyl; p represents an integer equal to 0 or 1; r represents an integer equal to 2 or 3 and r+p=3.
The polymerization step is carried out conventionally by anionic polymerization initiated, for example, by means of an organic compound of an alkali metal or alkaline earth metal. The anionic polymerization generates elastomer chains having a reactive site at the chain end. The term then commonly used is living elastomer or living chain.
In the context of an anionic polymerization, the polymerization initiator can be any known anionic initiator. An initiator containing an alkali metal, such as lithium, or an alkaline earth metal, such as barium, is preferably used. Suitable as lithium-containing initiators in particular are those comprising a carbon-lithium bond or a nitrogen-lithium bond. Representative compounds are aliphatic organolithium compounds, such as ethyllithium, n-butyllithium (n-BuLi) or isobutyllithium, and lithium amides obtained from a cyclic secondary amine, such as pyrrolidone and hexamethyleneimine. Such anionic polymerization initiators are known to those skilled in the art. Preferably, the polymerization initiator can be n-butyllithium.
The polymerization can be carried out in a way known per se, continuously or batchwise, and preferably continuously. The polymerization is generally carried out at temperatures of from 0° C. to 110° C. and preferably from 40° C. to 100° C., indeed even from 50° C. to 90° C. The polymerization process can be carried out in solution, in a more or less concentrated or dilute medium.
The organic polymerization solvent is preferably an inert hydrocarbon solvent which can, for example, be an aliphatic or alicyclic hydrocarbon, such as pentane, hexane, heptane, isooctane, cyclohexane, cyclopentane or methylcyclohexane, or an aromatic hydrocarbon, such as benzene, toluene or xylene.
It is possible to add, to the polymerization medium, a polar compound, preferably a compound belonging to the group consisting of diethers, diamines, tetrahydrofurans (such as THF), and tetrahydrofurfuryl ethers. Tetramethylethylenediamine is preferentially suitable as diamine. Particularly suitable as diethers are 1,2-diethoxyethane, 1,2-dimethoxyethane, and tetrahydrofurfuryl ethers such as tetrahydrofurfuryl ethyl ethers and tetrahydrofurfuryl propyl ethers.
The monomers which can be used in the context of the invention are defined above.
The anionic polymerization generates elastomer chains having a reactive site at the chain end. These living chains, or living elastomers, subsequently react with the modifying agent during the modification step. The modifying agent comprises more than one group reactive with respect to the reactive site of the elastomer, in this case alkoxy groups, aryloxy groups or halogen atoms substituting the Z atom.
The amount of modifying agent of formula (II) intended to react with the living diene elastomer depends essentially on the type of modified diene elastomer desired. In general, the molar ratio of groups of the modifying agent of formula (II) that are reactive with respect to the living elastomer, to the metal of the polymerization initiator, is at least 0.05, preferably at least 0.10, more preferentially at least 0.15, and at most 0.70, preferentially at most 0.60.
Thus, according to a particularly advantageous variant of the modification step, the molar ratio of the modifying agent of formula (II) to the metal of the polymerization initiator has a value within a range extending from 0.20 to 0.55.
The conditions for addition of the modifying agent of formula (II) to the diene elastomer and for reaction thereof with said diene elastomer are conventional as regards modification in anionic polymerization and are known to a person skilled in the art. These conditions do not comprise specific limitations.
For example, this reaction with the living diene elastomer can take place at a temperature of between −20° C. and 100° C., by addition of the modifying agent to the living elastomer chains, or vice versa. This reaction can, of course, be carried out with one or more different modifying agents.
Preferably, the organic solvent used during the step of modifying the diene elastomer with the modifying agent is the same as that used during the anionic polymerization step.
The mixing of the living elastomer with the modifying agent can be carried out by any suitable means, in particular using any mixer having available stirring of static type and/or any dynamic mixer of perfectly stirred type known to those skilled in the art. The latter determines the reaction time between the living diene polymer and the modifying agent, which can vary from a few minutes, for example 2 minutes, to several hours, for example 2 hours.
Mention may be made, as modifying agent of formula (II) of which the function capable of interacting with a reinforcing filler is an amine, of (N,N-dialkylaminopropyl)trialkoxysilanes, (N,N-dialkylaminopropyl)alkyldialkoxysilanes, (N-alkylaminopropyl)trialkoxysilanes and (N-alkylaminopropyl)alkyldialkoxysilanes, the secondary amine function of which is protected by a trialkylsilyl group, and aminopropyltrialkoxysilanes and aminopropylalkyldialkoxysilanes, the primary amine function of which is protected by two trialkylsilyl groups. The alkyl substituents present on the nitrogen atom are linear or branched and advantageously have from 1 to 10 carbon atoms, preferably 1 to 4, more preferentially 1 or 2. Suitable, for example, as alkyl substituents are the methylamino-, dimethylamino-, ethylamino-, diethylamino-, propylamino-, dipropylamino-, butylamino-, dibutylamino-, pentylamino-, dipentylamino, hexylamino, dihexylamino or hexamethyleneimino groups, preferably the diethylamino and dimethylamino groups. The alkoxy substituents are linear or branched and generally have from 1 to 10 carbon atoms, indeed even 1 to 8, preferably from 1 to 4 and more preferentially 1 or 2.
Preferentially, the modifying agent of formula (II) can be selected from (3-N,N-dialkylaminopropyl)trialkoxysilanes and (3-N,N-dialkylaminopropyl)alkyldialkoxysilanes, the alkyl group being the methyl or ethyl group and the alkoxy group being the methoxy or ethoxy group.
Preferentially, the modifying agent of formula (II) can be selected from (3-N,N-alkyltrimethylsilylaminopropyl)trialkoxysilanes and (3-N,N-alkyltrimethylsilylaminopropyl)alkyldialkoxysilanes, the alkyl group being the methyl or ethyl group and the alkoxy group being the methoxy or ethoxy group.
Preferentially, the modifying agent of formula (II) can be selected from (3-N,N-bistrimethylsilylaminopropyl)trialkoxysilanes and (3-N,N-bistrimethylsilylaminopropyl)alkyldialkoxysilanes, the alkyl group being the methyl or ethyl group and the alkoxy group being the methoxy or ethoxy group.
Preferentially, the modifying agent of formula (II) can be selected from (3-N,N-dimethylaminopropyl)trimethoxysilane, (3-N,N-dimethylaminopropyl)triethoxysilane, (3-N,N-diethylaminopropyl)trimethoxysilane, (3-N,N-diethylaminopropyl)triethoxysilane, (3-N,N-dipropyl aminopropyl)trimethoxysilane, (3-N,N-dipropylaminopropyl)triethoxysilane, (3-N,N-dibutylaminopropyl)trimethoxysilane, (3-N,N-dibutylaminopropyl)triethoxysilane, (3-N,N-dipentylaminopropyl)trimethoxysilane, (3-N,N-dipentylaminopropyl)triethoxysilane, (3-N,N-dihexylaminopropyl)trimethoxysilane, (3-N,N-dihexylaminopropyl)triethoxysilane, (3-hexamethyleneaminopropyl)trimethoxysilane, (3-hexamethyleneaminopropyl)triethoxysilane, (3-morpholinopropyl)trimethoxysilane, (3-morpholinopropyl)triethoxysilane, (3-piperidinopropyl)trimethoxysilane or (3-piperidinopropyl)triethoxysilane. More preferentially, the modifying agent of formula (II) is (3-N,N-dimethylaminopropyl)trimethoxysilane. Preferentially, the modifying agent of formula (II) can be selected from (3-N,N-methyltrimethylsilylaminopropyl)trimethoxysilane, (3-N,N-methyltrimethylsilylaminopropyl)triethoxysilane, (3-N,N-ethyltrimethylsilylaminopropyl)trimethoxysilane, (3-N,N-ethyltrimethylsilylaminopropyl)triethoxysilane, (3-N,N-propyltrimethylsilylaminopropyl)trimethoxysilane or (3-N,N-propyltrimethylsilylaminopropyl)triethoxysilane. More preferentially, the modifying agent of formula (II) is (3-N,N-methyltrimethylsilylaminopropyl)trimethoxysilane.
According to another embodiment, the function capable of interacting with a reinforcing filler is an isocyanate function. Preferentially, the modifying agent of formula (II) can be selected from (3-isocyanatopropyl)trialkoxysilanes and (3-isocyanatopropyl)alkyldialkoxysilanes, the alkyl group being the methyl or ethyl group and the alkoxy group being the methoxy or ethoxy group. More preferentially still, the modifying agent of formula (II) is (3-isocyanatopropyl)dimethylaminopropyl)trimethoxysilane and (3-isocyanatopropyl)triethoxysilane.
According to another embodiment, the function capable of interacting with a reinforcing filler is an imine function. Preferentially, the modifying agent of formula (II) can be selected from N-(1,3-dimethylbutylidene)-3-(trimethoxysilyl)-1-propanamine, N-(1,3-dimethylbutylidene)-3-(triethoxysilyl)-1-propanamine, N-(1,3-methylethylidene)-3-(trimethoxysilyl)-1-propanamine, N-(1,3-methylethylidene)-3-(triethoxysilyl)-1-propanamine, N-ethylidene-3-(trimethoxysilyl)-1-propanamine, N-ethylidene-3-(triethoxysilyl)-1-propanamine, N-(1-methylpropylidene)-3-(trimethoxysilyl)-1-propanamine, N-(1-methylpropylidene)-3-(triethoxysilyl)-1-propanamine, N-(4-N,N-dimethylaminobenzylidene)-3-(trimethoxysilyl)-1-propanamine, N-(4-N,N-dimethylaminobenzylidene)-3-(triethoxysilyl)-1-propanamine, N-(cyclohexylidene)-3-(trimethoxysilyl)-1-propanamine, N-(cyclohexylidene)-3-(triethoxysilyl)-1-propanamine, N-(3-trimethoxysilylpropyl)-4,5-dihydroimidazole, N-(3-triethoxysilylpropyl)-4,5-dihydroimidazole, N-(3-trimethoxysilylpropyl)-4,5-imidazole and N-(3-triethoxysilylpropyl)-4,5-imidazole.
According to another embodiment, the function capable of interacting with a reinforcing filler is a cyano function. Preferentially, the modifying agent of formula (II) can be selected from (3-cyanopropyl)trialkoxysilanes and (3-cyanopropyl)alkyldialkoxysilanes, the alkyl group being the methyl or ethyl group and the alkoxy group being the methoxy or ethoxy group. More preferentially, the modifying agent of formula (II) can be selected from (3-cyanopropyl)trimethoxysilane and (3-cyanopropyl)triethoxysilane.
According to another embodiment, the function capable of interacting with a reinforcing filler is a protected or unprotected function derived from thiol —SR, R being a protecting group or H. As examples, mention may be made of (S-trialkylsilylmercaptopropyl)trialkoxysilanes and (S-trialkylsilylmercaptopropyl)alkyldialkoxysilanes, the alkyl group on the silicon atom bearing alkoxysilane groups being the methyl or ethyl group and the alkoxy group being the methoxy or ethoxy group. The alkyl group on the silicon bonded to the sulfur atom is the methyl or tert-butyl group. Preferentially, the modifying agent of formula (II) can be selected from (S-trimethylsilylmercaptopropyl)trimethoxysilane, (S-trimethylsilylmercaptopropyl)triethoxysilane, (S-tert-butyldimethylsilylmercaptopropyl)trimethoxysilane and (S-tert-butyldimethylsilylmercaptopropyl)triethoxysilane.
According to another embodiment, the function capable of interacting with a reinforcing filler is a carboxylate function. Mention may be made, as carboxylate function, of acrylates or methacrylates. Such a function is preferably a methacrylate. Preferentially, the modifying agent of formula (II) can be selected from (3-methacryloyloxypropyl)trialkoxysilanes and (3-methacryloyloxypropyl)alkyldialkoxysilanes, the alkyl group being the methyl or ethyl group and the alkoxy group being the methoxy or ethoxy group. Preferentially, the modifying agent can be selected from (3-methacryloyloxypropyl)trimethoxysilane and (3-methacryloyloxypropyl)triethoxysilane.
According to another embodiment, the function capable of interacting with a reinforcing filler is an epoxide function. Preferentially, the modifying agent of formula (II) can be selected from (3-glycidyloxypropyl)trialkoxysilanes and (3-glycidyloxypropyl)alkyldialkoxysilanes, the alkyl group being the methyl or ethyl group and the alkoxy group being the methoxy or ethoxy group. Preferentially, the modifying agent can be selected from (2-glycidyloxyethyl)trimethoxysilane, (2-glycidyloxyethyl)triethoxysilane, (3-glycidyloxypropyl)trimethoxysilane, (3-glycidyloxypropyl)triethoxysilane, 2-(3,4-epoxycyclohexyl)ethyltrimethoxysilane or 2-(3,4-epoxycyclohexyl)ethyltriethoxysilane.
According to another embodiment, the function capable of interacting with a reinforcing filler is a protected or unprotected primary phosphine function, a protected or unprotected secondary phosphine function or a tertiary phosphine function. Preferentially, the modifying agent of formula (II) can be selected from (3-P,P-bistrimethylsilylphosphinopropyl)trialkoxysilanes, (3-P,P-bistrimethylsilylphosphinopropyl)alkyldialkoxysilanes, (3-P,P-alkyltrimethylsilylphosphinopropyl)trialkoxysilanes, (3-P,P-alkyltrimethylsilylphosphinopropyl)alkyldialkoxysilanes, (3-P,P-dialkylphosphinopropyl)trialkoxysilanes and (3-P,P-dialkylphosphinopropyl)alkyldialkoxysilanes, the alkyl group being the methyl, ethyl or phenyl group and the alkoxy group being the methoxy or ethoxy group. Preferentially, the modifying agent of formula (II) can be selected from (3-P,P-bistrimethylsilylphosphinopropyl)trimethoxysilane, (3-P,P-bistrimethylsilylphosphinopropyl)triethoxysilane, (3-methyltrimethylsilylphosphinopropyl)trimethoxysilane, (3-methyltrimethylsilylphosphinopropyl)triethoxysilane, (3-ethyltrimethylsilylphosphinopropyl)trimethoxysilane, (3-ethyltrimethylsilylphosphinopropyl)triethoxysilane, (3-dimethylphosphinopropyl)trimethoxysilane, (3-dimethylphosphinopropyl)triethoxysilane, (3-diethylphosphinopropyl)trimethoxysilane, (3-diethylphosphinopropyl)triethoxysilane, (3-ethylmethylphosphinopropyl)trimethoxysilane, (3-ethylmethylphosphinopropyl)triethoxysilane, (3-diphenylphosphinopropyl)trimethoxysilane and (3-diphenylphosphinopropyl)triethoxysilane.
When in formula (II) q=0, mention may then be made, as examples of modifying agent, of compounds such as tin tetrachloride, methyltin trichloride, dimethyltin dichloride, dibutyltin dichloride, tetrachlorosilane, methyltrichlorosilane and dimethyldichlorosilane, tetraalkoxysilanes which are such that each alkyl group comprises from 1 to 10 carbon atoms, preferably from 1 to 4 carbon atoms, trialkyl phosphites which are such that each alkyl group comprises from 1 to 10 carbon atoms or triaryl phosphites which are such that each aryl group comprises from 6 to 12 carbon atoms, the aryl groups possibly being substituted by one or more C1-C6 alkyls; preferably substituted by one or more t-butyl groups. As particularly preferred modifying agent of formula (II), mention may be made of dimethyltin, dibutyltin dichloride, tetrachlorosilane, methyltrichlorosilane, dimethyldichlorosilane, tris(nonylphenyl) phosphite and tris(2,4-di(tert-butyl)phenyl) phosphite.
The plasticizing resin as mentioned above is added to the polymerization and modification medium. It is added in the same way as that mentioned in the first variant of the process for manufacturing the resin-extended modified diene elastomer.
Likewise, the solvent in which the modified diene elastomer mixture and the plasticizing resin are located is removed in the same way as that mentioned in the first variant of the process for manufacturing the resin-extended modified diene elastomer. It is therefore possible to perform, for example, steam stripping. The resin-extended modified diene elastomer according to the invention can potentially be washed, dried and shaped into balls, in particular for its storage and its later use.
Preferentially, in the two variants of the process for manufacturing the resin-extended modified diene elastomer, it is possible, before the step of removing the organic solvent, to add an extender oil. Suitable in particular as extender oil are the plasticizing oils selected from the group consisting of naphthenic oils (low- or high-viscosity, in particular hydrogenated or non-hydrogenated), paraffinic oils, MES (Medium Extracted Solvate) oils, TDAE (Treated Distillate Aromatic Extract) oils, RAE (Residual Aromatic Extract) oils, TRAE (Treated Residual Aromatic Extract) oils and SRAE (Safety Residual Aromatic Extract) oils, mineral oils, plant oils, preferably those comprising triglycerides, ether plasticizers, ester plasticizers, phosphate plasticizers, sulfonate plasticizers and the mixtures of these compounds. The extender oil content added will always be lower than the resin content added to the modified diene elastomer in solution.
More preferentially, the process for manufacturing the resin-extended modified diene elastomer, irrespective of the variant used, does not comprise adding a plasticizing oil before removing the organic solvent.
Rubber composition comprising the resin-extended modified diene elastomer
The modified diene elastomer of the invention as defined above can be used in any rubber compositions, in particular those intended for the manufacture of semi-finished articles for tyres and for the manufacture of tyres.
Thus, another subject of the present invention relates to a rubber composition based on at least one resin-extended modified diene elastomer as defined above or capable of being obtained by the process as defined above, a reinforcing filler and a crosslinking system.
Use may be made of any type of “reinforcing” filler known for its abilities to reinforce a rubber composition which can be used in particular for the manufacture of tyres, for example an organic filler, such as carbon black, an inorganic filler, such as silica, or else a mixture of these two types of fillers.
Suitable as carbon blacks are all carbon blacks, in particular the blacks conventionally used in tyres or their treads. Among the latter, mention will be made more particularly of the reinforcing carbon blacks of the 100, 200 and 300 series, or the blacks of the 500, 600 or 700 series (ASTM D-1765-2017 grades), for instance the N115, N134, N234, N326, N330, N339, N347, N375, N550, N683 and N772 blacks. These carbon blacks may be used in isolated form, as commercially available, or in any other form, for example as support for some of the rubber additives used. The carbon blacks might, for example, be already incorporated in the diene elastomer, in particular isoprene elastomer, in the form of a masterbatch (see, for example, application WO97/36724-A2 or WO99/16600-A1).
“Reinforcing inorganic filler” should be understood here as meaning any inorganic or mineral filler, whatever its colour and its origin (natural or synthetic), also referred to as “white” filler, “clear” filler or even “non-black” filler, in contrast to carbon black, capable of reinforcing, by itself alone, without means other than an intermediate coupling agent, a rubber composition intended for the manufacture of tyres. In a known way, some reinforcing inorganic fillers can be characterized in particular by the presence of hydroxyl (—OH) groups at their surface.
Suitable in particular as reinforcing inorganic fillers are mineral fillers of the siliceous type, preferentially silica (SiO2), or of the aluminous type, in particular alumina (Al2O3). The silica used can be any reinforcing silica known to those skilled in the art, in particular any precipitated or fumed silica having a BET specific surface area and also a CTAB specific surface area both of less than 450 m2/g, preferably within a range extending from 30 to 400 m2/g, in particular from 60 to 300 m2/g. Any type of precipitated silica, in particular highly dispersible precipitated silicas (referred to as “HDS” for “highly dispersible” or “highly dispersible silica”), can be used. These precipitated silicas, which are or are not highly dispersible, are well known to those skilled in the art. Mention may be made, for example, of the silicas described in patent applications WO03/016215-A1 and WO03/016387-A1. Use may in particular be made, among commercial HDS silicas, of the Ultrasil® 5000GR and Ultrasil® 7000GR silicas from Evonik or the Zeosil® 1085GR, Zeosil® 1115 MP, Zeosil® 1165MP, Zeosil® Premium 200MP and Zeosil® HRS 1200 MP silicas from Solvay. Use may be made, as non-HDS silica, of the following commercial silicas: the Ultrasil® VN2GR and Ultrasil® VN3GR silicas from Evonik, the Zeosil® 175GR silica from Solvay or the Hi-Sil EZ120G(-D), Hi-Sil EZ160G(-D), Hi-Sil EZ200G(-D), Hi-Sil 243LD, Hi-Sil 210 and Hi-Sil HDP 320G silicas from PPG.
According to an advantageous variant of the invention, the reinforcing filler is predominantly silica, that is to say that it comprises more than 50% by weight, of the total weight of the reinforcing filler, of silica.
The use of silica as reinforcing filler may require the use of a coupling agent in order to establish the connection between the filler and the elastomer. It is then possible to use, as coupling agents, organosilanes, in particular alkoxysilane polysulfides or mercaptosilanes, or also at least bifunctional polyorganosiloxanes.
Such a coupling agent should not be confused with the modifying agent used for the synthesis of the modified diene elastomer described above.
The rubber composition according to the invention can also in addition contain coupling activators, agents for covering the fillers or more generally processing aids capable, in a known way, by virtue of an improvement in the dispersion of the reinforcing filler within the resin-extended modified diene elastomer and of a lowering of the viscosity of the composition, of improving its ability to be processed in the raw state, these agents being, for example, hydrolysable silanes, such as alkylalkoxysilanes, polyols, polyethers, primary, secondary or tertiary amines, or hydroxylated or hydrolysable polyorganosiloxanes.
The rubber composition according to the invention can also additionally contain at least one plasticizer. In a way known to those skilled in the art of tyre rubber compositions, this plasticizer is preferably selected from resins with a high glass transition temperature (Tg), low-Tg resins, plasticizing oils and mixtures thereof. Preferably, the plasticizer is chosen from high-Tg resins, plasticizing oils and mixtures thereof. When the rubber composition also comprises a high-Tg resin, this resin can be identical to that used for the extension of the modified elastomer or can be of a different chemical nature.
By definition, a high-Tg resin is solid at ambient temperature (23° C. and 1 atm), a plasticizing oil is liquid at ambient temperature and a low-Tg hydrocarbon resin is viscous at ambient temperature. The Tg is measured according to standard ASTM D3418 (2008).
In a known way, the high-Tg hydrocarbon resins are thermoplastic resins, the Tg of which is greater than 20° C. The preferential high-Tg resins which can be used in the context of the invention are well known to those skilled in the art and are commercially available.
The plasticizer can optionally comprise a resin which is viscous at 20° C., referred to as “low-Tg” resin, that is to say which, by definition, has a Tg within a range between −40° C. and 20° C.
The plasticizer can also contain a plasticizing oil (or extender oil) which is liquid at 20° C., referred to as “low Tg”, that is to say which, by definition, has a Tg of less than 20° C., preferably of less than 40° C.
Any extender oil, whether it is of aromatic or non-aromatic nature, known for its plasticizing properties with regard to elastomers can be used. Suitable in particular are the plasticizing oils selected from the group consisting of naphthenic oils (low- or high-viscosity, in particular hydrogenated or non-hydrogenated), paraffinic oils, IVIES (Medium Extracted Solvate) oils, TDAE (Treated Distillate Aromatic Extract) oils, RAE (Residual Aromatic Extract) oils, TRAE (Treated Residual Aromatic Extract) oils and SRAE (Safety Residual Aromatic Extract) oils, mineral oils, plant oils, ether plasticizers, ester plasticizers, phosphate plasticizers, sulfonate plasticizers and the mixtures of these compounds.
The rubber composition in accordance with the invention can additionally also comprise all or some of the usual additives and processing aids known to those skilled in the art and generally used in rubber compositions for tyres, in particular rubber compositions of treads, such as, for example, non-reinforcing fillers, pigments, protective agents, such as antiozone waxes, chemical antiozonants or antioxidants, anti-fatigue agents or reinforcing resins (such as described, for example, in application WO 02/10269).
The rubber composition according to the invention comprises at least one crosslinking system, for example based on sulfur and other vulcanizing agents, and/or peroxide and/or bismaleimide.
The rubber composition in accordance with the invention is manufactured in appropriate mixers using two successive preparation phases well known to those skilled in the art:
The final composition thus obtained is subsequently calendered, for example in the form of a sheet or of a slab, in particular for a laboratory characterization, or else extruded in the form of a rubber semi-finished product (or profiled element) which can be used, for example, as a vehicle tyre tread.
The composition may be either in the raw state (before crosslinking or vulcanization) or in the cured state (after crosslinking or vulcanization), and may be a semi-finished product which can be used in a tyre.
The crosslinking of the composition can be carried out in a manner known to those skilled in the art, for example at a temperature of between 130° C. and 200° C., under pressure.
Due to the maintenance of the compromise of hysteresis properties/raw processability/quality of its extrudate, it will be noted that such a composition according to the invention can constitute any semi-finished product of the tyre and particularly a tread.
Thus, another subject of the present invention relates to a semi-finished rubber article for a tyre comprising at least one crosslinkable or crosslinked composition as defined previously. Preferably, this semi-finished article is a tread.
Lastly, another subject of the present invention relates to the tyre comprising at least one rubber composition defined previously or a semi-finished article defined above.
A final subject of the invention is thus a tyre comprising a semi-finished article constituted, in all or in part, by a composition according to the invention, in particular a tread.
The invention, described in more detail above, relates to at least one of the embodiments listed in the following points:
Z(R2)p(T)r(R3-Y)q (II)
The abovementioned characteristics of the present invention, and also others, will be better understood on reading the following description of several exemplary embodiments of the invention, which are given as nonlimiting illustrations.
The characteristics of the elastomers, resins, oils and compositions are determined according to the methods described above.
Preparation of the polymer A: Non-resin-extended modified functional SBR— control
A continuously fed, stirred 32.5 litre reactor is continuously charged with methylcyclohexane at a mass flow rate of 64.00 kg·h−1, with butadiene at a mass flow rate of 8.06 kg·h−1, with styrene at a mass flow rate of 1.59 kg·h−1 and 55 ppm of tetrahydrofurfuryl ethyl. The concentration by mass of monomer is 13% by weight.
n-Butyllithium (n-BuLi) is introduced in a sufficient amount in order to neutralize the protic impurities introduced by the different constituents present in the reactor input.
670 μmol of n-BuLi per 100 g of monomers are introduced at the inlet of the reactor.
The different flow rates are calculated in order for the mean residence time in the reactor to be 20 min. The temperature is maintained at 90° C.
A sample of polymer solution is withdrawn at the outlet of the polymerization reactor. The polymer is subsequently subjected to an antioxidizing treatment with addition of 0.40 phr of 2,2′-methylenebis(4-methyl-6-(tert-butyl)phenol) and 0.2 phr of N-(1,3-dimethylbutyl)-N′-phenyl-p-phenylenediamine. The degree of conversion obtained at this step is 95% by weight. It is determined by dry extract at 140° C. under reduced pressure of 200 mmHg.
The polymer thus treated is subsequently separated from its solution by a steam stripping operation and then dried on an open mill at 100 C. The characteristics of the polymer obtained at this step, that is to say the initial inherent viscosity, the initial Mn, the initial Mw and the initial PDI (PDI=polydispersity index), are given in Table 2.
At the outlet of the polymerization reactor, at a temperature equal to 90° C., 194.00 μmol of hexamethylcyclotrisiloxane in solution in methylcyclohexane per 100 g of monomers are added to the living polymer solution (hexamethylcyclotrisiloxane/lithium ratio=0.29) and also 30 μmol of tin tetrachloride in solution in methylcyclohexane per 100 g of monomers (tin tetrachloride/lithium molar ratio=0.04). The mixing is carried out in a static mixer of SMX type consisting of 20 elements followed by tubing for a residence time of at least 2.5 minutes.
The polymer thus obtained is subjected to an antioxidizing treatment with addition of 0.4 phr of 2,2′-methylenebis(4-methyl-6-(tert-butyl)phenol) and 0.2 phr of N-(1,3-dimethylbutyl)-N′-phenyl-p-phenylenediamine. The polymer thus treated is subsequently separated from its solution by a steam stripping operation and then dried on an open mill at 100 C. The characteristics of the polymer obtained at this step, that is to say the final inherent viscosity, the final Mn, the final Mw and the final PDI, are given in Table 2.
Preparation of the polymer B: Resin-extended unmodified functional SBR— control
A continuously fed, stirred 32.5 litre reactor is continuously charged with methylcyclohexane at a mass flow rate of 32.40 kg·h−1, with butadiene at a mass flow rate of 3.07 kg·h−1, with styrene at a mass flow rate of 0.63 kg·h−1 and 49 ppm of tetrahydrofurfuryl ethyl ether. The concentration by mass of monomer is equal to 10% by weight.
n-Butyllithium is introduced in a sufficient amount in order to neutralize the protic impurities introduced by the different constituents present in the reactor input.
475 μmol of n-BuLi per 100 g of monomers are introduced at the inlet of the reactor.
The different flow rates are calculated in order for the mean residence time in the reactor to be 40 min. The temperature is maintained at 90° C.
A sample of polymer solution is withdrawn at the outlet of the polymerization reactor. The polymer is subsequently subjected to an antioxidizing treatment with addition of 0.4 phr of 2,2′-methylenebis(4-methyl-6-(tert-butyl)phenol) and 0.2 phr of N-(1,3-dimethylbutyl)-N′-phenyl-p-phenylenediamine. The degree of conversion obtained at this step is 93% by weight. It is determined by dry extract at 140° C. under reduced pressure of 200 mmHg. The polymer thus treated is subsequently separated from its solution by a steam stripping operation and then dried on an open mill at 100 C. The characteristics of the polymer obtained at this step, that is to say the initial inherent viscosity, the initial Mn, the initial Mw and the initial PDI, are given in Table 2.
At the outlet of the polymerization reactor, at a temperature equal to 90° C., 250 μmol of hexamethylcyclotrisiloxane in solution in methylcyclohexane per 100 g of monomers are added to the living polymer solution (hexamethylcyclotrisiloxane/lithium molar ratio=0.53). The mixing is carried out in a static mixer of SMX type consisting of 20 elements followed by tubing for a residence time of at least 2.5 minutes.
The polymer thus obtained is subjected to an antioxidizing treatment with addition of 0.4 phr of 2,2′-methylenebis(4-methyl-6-(tert-butyl)phenol) and 0.2 phr of N-(1,3-dimethylbutyl)-N′-phenyl-p-phenylenediamine. A homogeneous solution of functionalized styrene/butadiene copolymer in methylcyclohexane is obtained.
Subsequently, a solution prepared from Escorez 5600 resin from Exxon at 70% by weight in methylcyclohexane is added to the elastomeric solution previously obtained in an amount of 50 parts per 100 parts by weight of elastomer. Mixing is carried out in a static mixer consisting of 36 mixing elements of Kenics KMR type.
The mixture of unmodified elastomer/resin in methylcyclohexane is then separated from the methylcyclohexane solvent by a steam stripping operation, and then dried on an open mill at 100° C.
The characteristics of the resin-extended polymer obtained at this step, that is to say the final inherent viscosity, the final Mn, the final Mw and the final PDI, are given in Table 2.
Preparation of the polymer C: Resin-extended unmodified functional SBR— control
The procedure used to prepare polymer B is followed for preparing polymer C, except for the amounts of each of the components which differ. These amounts are shown in Table 1.
The characteristics of the polymer C obtained are presented in Table 2.
Preparation of the polymer D: Resin-extended modified functional SBR— according to the invention
A continuously fed, stirred 32.5 litre reactor is continuously charged with methylcyclohexane at a mass flow rate of 32.60 kg·h−1, with butadiene at a mass flow rate of 3.04 kg·h−1, with styrene at a mass flow rate of 0.67 kg·h−1 and 40 ppm of tetrahydrofurfuryl ethyl ether. The concentration by mass of monomer is equal to 10% by weight.
n-Butyllithium is introduced in a sufficient amount in order to neutralize the protic impurities introduced by the different constituents present in the reactor input.
335 μmol of n-BuLi per 100 g of monomers are introduced at the inlet of the reactor.
The different flow rates are calculated in order for the mean residence time in the reactor to be 40 min. The temperature is maintained at 90° C.
A sample of polymer solution is withdrawn at the outlet of the polymerization reactor. The polymer thus obtained is subjected to an antioxidizing treatment with addition of 0.4 phr of 2,2′-methylenebis(4-methyl-6-(tert-butyl)phenol) and 0.2 phr of N-(1,3-dimethylbutyl)-N′-phenyl-p-phenylenediamine.
The degree of conversion obtained at this step is 91% by weight. It is determined by dry extract at 140° C. under reduced pressure of 200 mmHg. The polymer thus treated is subsequently separated from its solution by a steam stripping operation and then dried on an open mill at 100 C. The characteristics of the polymer obtained at this step, that is to say the initial inherent viscosity, the initial Mn, the initial Mw and the initial PDI, are given in Table 2.
At the outlet of the polymerization reactor, at a temperature equal to 90° C., 145 μmol per 100 g of monomers of (N,N-dimethylaminopropyl)trimethoxysilane in solution in methylcyclohexane are added to the living polymer solution ((N,N-dimethylaminopropyl)trimethoxysilane/lithium molar ratio=0.43). The mixing is carried out in a static mixer of SMX type consisting of 20 elements followed by tubing for a residence time of at least 2.5 minutes.
The polymer thus obtained is subjected to an antioxidizing treatment with addition of 0.6 phr of 2,2′-methylenebis(4-methyl-6-(tert-butyl)phenol) and 0.2 phr of N-(1,3-dimethylbutyl)-N′-phenyl-p-phenylenediamine. A homogeneous solution of functional and modified styrene/butadiene copolymer is obtained. Subsequently, a solution prepared from Escorez 5600 resin from Exxon at 70% by weight in methylcyclohexane is added to the elastomeric solution in an amount of 48 parts per 100 parts by weight of elastomer.
The mixture of modified diene elastomer/resin in methylcyclohexane is then separated from the methylcyclohexane by a steam stripping operation, and then dried on an open mill at 100° C.
The characteristics of the resin-extended polymer D obtained at this step, that is to say the final inherent viscosity, the final Mn, the final Mw and the final PDI, are given in Table 2.
Preparation of the polymer E: Resin-extended modified functional SBR— according to the invention
The procedure used to prepare polymer D is followed for obtaining polymer E, except for the amounts of each of the components which are modified. These amounts are mentioned in Table 1.
The characteristics of the polymer E obtained are given in Table 2.
Preparation of the polymer F: Resin-extended modified functional BR— according to the invention
The procedure used to prepare polymer D is followed for obtaining polymer F, except for the nature and the amounts of each of the components which are modified. Additionally, no styrene is added to the reactor. These amounts are mentioned in Table 1.
The characteristics of the polymer F obtained are given in Table 2.
Preparation of the polymer G: Resin-extended modified non-functional SBR— according to the invention
The procedure used to prepare polymer D is followed for obtaining polymer G, except for the nature and the amounts of each of the components which are modified and except for the replacement of the (N,N-dimethylaminopropyl)trimethoxysilane with tris(2,4-di(tert-butyl)phenyl) phosphite. These amounts are mentioned in Table 1.
The characteristics of the polymer G obtained are given in Table 2.
(1) The Tg of the polymer, with the exception of polymer A which is not extended, is measured before the addition of the resin
Example of preparation of the compositions of rubber compositions:
The elastomers A to F were used to prepare rubber compositions of tread type, each comprising silica as reinforcing filler.
The formulations are expressed as percentage by weight per 100 parts by weight of elastomer (phr) and are presented in Table 3.
All compositions have, in the end, the same resin content, namely 61 phr.
Each of the following compositions is produced, in a first step, by thermomechanical working and then, in a second, “finishing step”, by mechanical working.
The elastomer, resin-extended or otherwise, two-thirds of the silica, the coupling agent, the diphenylguanidine and the carbon black are introduced into a laboratory internal mixer of “Banbury” type which has a capacity of 400 cm3, which is 72% filled and which has an initial temperature of 90° C.
The thermomechanical working is carried out by means of blades, the mean speed of which is 50 rpm and the temperature of which is 90° C.
After one minute, the final third of the silica, the antioxidant, the stearic acid, the TDAE oil and the resin are introduced, still under thermomechanical working.
After two minutes, the zinc oxide is introduced, the speed of the blades being 50 rpm.
The thermomechanical working is carried out for a further two minutes, up to a maximum dropping temperature of approximately 160° C.
The mixture thus obtained is recovered and cooled and then, in an external mixer (homofinisher), the sulfur and the sulfenamide are added at 30° C., the combined mixture being further mixed for a time of 3 to 4 minutes (second step of mechanical working).
The compositions thus obtained are subsequently calendered, either in the form of slabs (with a thickness ranging from 2 to 3 mm) or thin sheets of rubber, for the measurement of their physical or mechanical properties, or in the form of profiled elements which can be used directly, after cutting and/or assembling to the desired dimensions, for example as semi-finished products for tyres, in particular for treads.
These compositions are crosslinked at 150° C. for 40 min.
The results of the mechanical properties of the compositions are presented in Table 4 along with the quality of the extrudate.
As expected, control composition C2 exhibits tackiness properties that are lower than that of control composition C1, which represents a rubber composition used as a tread. However, the hysteresis properties are unchanged with respect to composition C1.
When the number-average molar mass of the resin-extended unmodified polymer is increased (polymer C), it is found that the composition C3 has tacky properties that are lower than that of the control composition C1 with an extrudate quality that is lower but which remains acceptable for tread use. However, the hysteresis properties of composition C3 are unchanged with respect to control compositions C1 and C2.
Surprisingly, and against all expectations, when the number-average molar mass of the polymer is increased further by modifying it (polymers D, E, F and G), it is found that the compositions according to the invention containing such resin-extended modified polymers exhibit, with respect to control compositions C2 to C3, both a significant reduction in tackiness properties and a significant improvement in hysteresis properties. The compositions of the invention I1 to 14 are on average two times less tacky than the control compositions C2 and C3 (reduction of more than 50% in tackiness). The compositions I1 to I4 of the invention are therefore more easily processable and also make it possible to produce tyres having improved rolling resistance compared to the control compositions. Advantageously, composition I4, in addition to better processability, also has an extrudate of better quality compared to control compositions C1 and C3.
The examples above show that the compositions comprising a diene elastomer according to the invention, that is to say a resin-extended functionalized or non-functionalized modified diene elastomer having a high number-average molar mass exhibit improved hysteresis properties as well as better processability without a degradation in the quality of their extrudates.
| Number | Date | Country | Kind |
|---|---|---|---|
| 2100884 | Jan 2021 | FR | national |
| Filing Document | Filing Date | Country | Kind |
|---|---|---|---|
| PCT/FR2022/050079 | 1/14/2022 | WO |
