| HS Code | 998953 |
| Softening Point | 115 °C (Ring & Ball) |
| Gardner Color | <1 (50% in toluene) |
| Appearance | Water-white pastille |
| Melt Viscosity | Approximately 150 mPa·s at 200 °C |
| Density | 1.09 g/cm³ at 25 °C |
| Acid Value | <1 mg KOH/g |
| Glass Transition Temperature | Approximately 55 °C |
| Number Average Molecular Weight | Approximately 800 g/mol |
| Flash Point | >200 °C |
| Refractive Index | Approximately 1.54 at 25 °C |
| Solubility | Soluble in aromatic and aliphatic hydrocarbons |
| Ash Content | <0.02% |
As an accredited High-Soften-Point Kristalex 3115LV Hydrocarbon Resin for Rubber factory, we enforce strict quality protocols—every batch undergoes rigorous testing to ensure consistent efficacy and safety standards.
| Packing | High-Soften-Point Kristalex 3115LV Hydrocarbon Resin for Rubber is packaged in 25 kg multi-layer paper bags for safe handling and storage. |
| Container Loading (20′ FCL) | 20′ FCL container loading of High-Soften-Point Kristalex 3115LV hydrocarbon resin for rubber, packed on pallets. |
| Shipping | Ship High-Soften-Point Kristalex 3115LV Hydrocarbon Resin in sealed, moisture-resistant bags on pallets. Protect from direct heat, humidity, and prolonged UV exposure. Non-hazardous under normal transport conditions, but avoid dust generation. Use covered, dry containers or trucks, and keep upright to prevent bag damage during handling. |
| Storage | Store High-Soften-Point Kristalex 3115LV Hydrocarbon Resin in a cool, dry, well-ventilated area away from heat, sparks, open flames, and strong oxidizers. Keep containers tightly sealed when not in use to prevent moisture ingress and contamination. Protect from direct sunlight and avoid generating dust. Maintain stable temperatures to preserve resin properties and ensure safe handling. |
| Shelf Life | Shelf life is typically 24 months from manufacture when stored unopened in original packaging, in a dry, cool area. |
In high-speed passenger car radial tread formulations, Kristalex 3115LV is introduced at 3.0–7.0 phr as a high-softening-point hydrocarbon resin that shifts tan δ at 0 °C upward while moderating the 60 °C loss modulus penalty when the silica network has been sufficiently silanized with bis[3-(triethoxysilyl)propyl] tetrasulfide. The nominal softening point of 150 °C and the narrow molecular weight distribution support transfer across the silica-silane interface without excessive tack generation in the final mixed batch. The industry compliance envelope for this application is dominated by ECE R117.03 for wet grip, exterior noise, and rolling resistance, in parallel with ISO 28580:2018 for rolling resistance coefficient measurements and ISO 4649:2017 for abrasion characteristics. Tensile verification follows ISO 37:2017, hardness is recorded under ASTM D2240-15, and Mooney viscosity is checked per ASTM D1646-19. Production-scale tangential internal mixers with ram pressure of 0.5–0.7 MPa and rotor speeds of 40–60 rpm receive the resin in the first masterbatch pass after carbon black and silica, so that shear heat reaches 145–155 °C and the resin disperses before the drop door opens; exceeding 165 °C during the same pass has been observed on multiple tire lines to cause excessive resin melt viscosity reduction, making the batch stick to the rotor end plates and producing non-uniform Mooney values between adjacent batches. The final mix is normally run at 30–45 rpm with curatives added at 95–105 °C, and rheometer cure curves are recorded under ASTM D5289-19 to detect scorch shifts. Above 7.0 phr with conventional paraffinic oil, the 60 °C loss modulus rises enough to erase the benefit in EV-specific rolling resistance targets, but published data for this specific resin in EV-specific ribbed tread configurations is limited. Terminal articles include ultra-high-performance summer passenger tire treads, wet-grip optimized PCR treads, and EU label-A rolling resistance designs; the resin is not recommended for abrasion-grade winter friction compounds where the glass-transition shift can reduce low-temperature flexibility below the required -20 °C impact threshold.
Kristalex 3115LV is incorporated into bromobutyl-based inner liner compounds at 8.0–12.0 phr to raise compound viscosity enough for calender sheet formation without relying on high-structure carbon black alone, while the resin's aromatic character participates in the low-strain dynamic modulus needed for barrier-layer stiffness. The governing standards include ISO 2782-1:2018 for gas permeability under differential pressure, ISO 37:2017 for tensile stress-strain, and ASTM D395-18 for compression set, with automotive supply-chain conformance typically required to IATF 16949:2016 and substance reporting under REACH Annex XVII Entry 50. In a two-stage internal mixing procedure, the resin is added during the second pass at 110–125 °C because adding it too early in the first pass depresses the effective shear heating of the butyl phase and can delay carbon black incorporation; calender lines then process the compound at gauge tolerances of 0.8–1.2 mm and roll temperatures not exceeding 75 °C. A typical four-roll inverted L calender with 610 mm roll diameters operates at a line tension of 0.8–1.5 N/mm, and the resin must remain fully dispersed to avoid low-gauge thin spots that propagate into barrier-layer failures. The critical threshold concern is splice adhesion after calendar cutting: plant audits on truck radial inner liner lines indicate that when the resin addition exceeds 12.0 phr, edge splice failures in the green stage increase unless a secondary tackifier is added, because the resin raises the compound's glass transition without supplying the same tack contribution as a lower-softening-point tackifying resin. Terminal products include tubeless passenger car radial inner liners, truck-bus radial inner liners, and specialty air-permeation-resistant plies for run-flat tires; published data for Kristalex 3115LV in halogenated butyl blends with silica up to 25 phr remains limited, so pilot-scale permeability validation per ISO 2782-1:2018 is required before full production release.
| Downstream rubber article | Polymer matrix | Typical resin loading window | Controlling standard or regulation | Process boundary |
|---|---|---|---|---|
| Passenger car radial tread | SBR/BR-silica | 3.0–7.0 phr | ECE R117.03; ISO 28580:2018 | Dump temp ≤ 165 °C |
| Tubeless inner liner | Bromobutyl/CIIR | 8.0–12.0 phr | ISO 2782-1:2018; IATF 16949:2016 | Second-pass finish ≤ 125 °C |
| EPDM weatherseal | EPDM | 10.0–18.0 phr | SAE J200; ISO 3384-1:2019 | UHF profile surface ≤ 230 °C |
| NBR/PVC cable sheath | NBR/PVC blend | 5.0–12.0 phr | IEC 60502-1; EN 50363-3 | Kneader discharge ≤ 155 °C |
| Industrial roll cover | NBR/EPDM blend | 12.0–18.0 phr | ISO 7619-1; ASTM D2240-15 | Autoclave cure ≤ 140 °C |
| Anti-vibration mounting | NR/BR blend | 5.0–10.0 phr | ASTM D429 Method B; ISO 815-1:2019 | Injection mold temp 150–160 °C |
For EPDM door and glass-run weatherseal profiles, Kristalex 3115LV is applied at 10.0–18.0 phr to reduce compound viscosity in high-hardness formulations while improving filler wetting before continuous vulcanization. The compound must satisfy SAE J200 classification for heat resistance and compression set, with long-term compression set tested under ISO 815-1:2019 at 100 °C, stress-relaxation under ISO 3384-1:2019, and low-temperature brittleness under ASTM D746-18. On a 90 mm pin-barrel cold-feed extruder with L/D 16:1, the resin reduces die swell and improves surface definition, but at loadings above 18 phr the extrudate temperature at the die head can rise above 105 °C, producing melt fracture and variable profile dimensions in UHF-cured dense rubber lines; typical line speeds of 15–35 m/min require the outlet compound Mooney viscosity to remain above 45 ML(1+4) 100 °C to avoid sag during hot-air curing. The downstream process is usually continuous vulcanization through UHF microwave and hot-air tunnels followed by an air-cooled haul-off, with salt-bath curing used for complex glass-run channels where dimensional stability under the curvature is mandatory. The resin's high softening point contributes to collapse resistance of the unsupported extrudate before cure, but pre-drying is required at ambient relative humidity above 60% to avoid surface defects in thick-wall parts. Terminal products include door seals, glass run channels, trunk perimeter seals, and low-friction coated weatherseal components; field records from automotive weatherseal extrusion plants show that batch-to-batch variation in resin softening point of more than ±2 °C can shift the die swell ratio enough to require downstream profile adjustment, so incoming softening point verification per ASTM E28-18 is applied.
Kristalex 3115LV at 5.0–12.0 phr serves as a coalescing and hardness-modifying resin in NBR/PVC blends used for oil-resistant flexible cable sheathing, with the resin's compatibility with the PVC phase reducing micro-phase viscosity contrast during fluxing in a 70 mm Buss kneader operating at a discharge temperature of 145–155 °C. The relevant compliance standards are IEC 60502-1 for low-voltage cable mechanical performance, EN 50363-3 for sheathing compounds, and 2011/65/EU RoHS for restricted substances, while tensile measurements follow IEC 60811-501:2012 and oil resistance is evaluated under IEC 60811-404:2012. The process path continues from the kneader into a hot pelletizer and then a crosshead extruder where the sheathing is applied directly over the wire bundle; when resin addition exceeds 12.0 phr, the compound's Shore A hardness measured per ASTM D2240-15 increases by 3–5 points, but the low-temperature flexibility tested under IEC 60811-504 can fall below the required -40 °C bending threshold for arctic-grade cables. The addition window must be further narrowed if brominated flame retardants are present because the resin can intensify plate-out on downstream cooling troughs and capstan belts. Terminal articles include oil-resistant control cable sheaths, flexible portable power cable jackets, and industrial sensor cable sheaths where low smoke and reduced compound cost are simultaneously required; published data for this specific resin in colourable NBR/PVC cable jackets is limited, and plant trials should verify the absence of plate-out on calendering elements at the upper loading boundary.
Characteristically, industrial rubber roll compounds for paper, textile, and printing nip applications use Kristalex 3115LV at 12.0–18.0 phr to harden the coverstock without increasing filler loading beyond the point where elastic recovery and grinding quality deteriorate. The roll cover materials are specified under ISO 7619-1 for indentation hardness, ASTM D2240-15 for Shore D verification, and ISO 4649:2017 for abrasion resistance, while adhesive bond strength to the steel core is qualified according to ASTM D429 Method B. The production process employs open two-roll mills with a friction ratio of 1.20–1.25 and controlled roll surface temperatures of 50–65 °C to build up multiple plies over an adhesive-primed core, followed by autoclave vulcanization at 130–140 °C and final grinding on rotating cylindrical grinders; the high-softening-point resin increases green strength enough to prevent ply delamination during the wrapping stage, but above 18.0 phr the resin-rich surface generates tacky grinding swarf that loads the grinding wheel and produces visually detectable chatter marks. Terminal products include paper mill press rolls, textile squeezing rollers, printing press inking rollers, and industrial nip rolls where a Shore D hardness of 30–45 combined with low compression set is needed; published data for Kristalex 3115LV in cast polyurethane roll covers is not applicable because the resin is used in rubber-covered roll builds rather than polyurethane systems.
In rubber-to-metal anti-vibration mountings, Kristalex 3115LV is blended into NR/BR formulations at 5.0–10.0 phr to displace part of the process oil while maintaining compound flow into multi-cavity injection molds on transfer molding machines with clamp forces of 150–250 tonnes and injection pressures of 80–120 MPa. The bond performance is validated under ASTM D429 Method B for 90° peel, while the mechanical performance must satisfy ISO 815-1:2019 compression set at 70 °C, ISO 4662:2017 rebound resilience, and ISO 37:2017 tensile stress-strain; under-the-hood thermal exposure is pre-qualified with ISO 188:2011 air aging at 100 °C for 168 h. The resin is pre-dispersed in the NR phase before carbon black addition to avoid migration toward the primer interface; plant failure modes observed on suspension bushing lines indicate that at loadings above 10.0 phr, the initial rubber-to-metal peel strength drops below the internal release threshold of 5 kN/m because the resin concentrates in the boundary layer and restricts mechanical interlocking with the phosphated steel surface. Terminal articles include engine mounts, suspension bushings, strut mounts, and torque rod collars, where a high-softening-point resin with narrow molecular weight distribution is beneficial for reducing cold flow during warehouse storage but must not be combined with amine-based epoxy primers that can react prematurely with the resin during the 160–170 °C cure cycle.
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High-Soften-Point Kristalex 3115LV Hydrocarbon Resin for Rubber is a low molecular weight aromatic hydrocarbon resin supplied in pastillated or flake form. The grade is produced from purified aromatic monomer streams and stripped to controlled volatile content; the numerical designation corresponds to a nominal ring-and-ball softening point of 115 °C as tested by ASTM E28. In rubber formulations the resin is used as a high-softening-point processing resin and tackifier for natural rubber, styrene-butadiene rubber, butadiene rubber, and EPDM compounds. The material is characterized by low Gardner color measured under ASTM D1544, a narrow molecular weight distribution, and low residual volatile content. Because the resin is a low molecular weight aromatic oligomer rather than a high-molecular-weight elastomer, it modifies viscoelastic response, filler wetting, green strength, cure rheology, and the temperature dependence of loss tangent. These effects are achieved at addition levels commonly in the range of 2 phr to 15 phr, with the exact loading determined by filler system, cure system, and dynamic requirements of the end product.
Routine batch acceptance relies on ring-and-ball softening point measured under ASTM E28. The nominal target is 115 °C, but the actual release window should be taken from the certificate of analysis for each lot because lot-to-lot variation can interact with Mooney viscosity control in highly extended compounds. Gardner color is measured per ASTM D1544 and is typically below 1 for fresh material. Melt viscosity is measured at 190 °C using ASTM D3236; this value is a better predictor of processing behavior than softening point alone because it reflects both molecular weight and molecular weight distribution. Ash content is measured by ISO 3451-1 and should be low to minimize interactions with silane coupling agents. Volatile content should be confirmed from the supplier batch documentation because the LV designation represents a controlled low-volatility production target rather than a universal numerical limit.
The resin is added during masterbatch or final mixing. Prior to addition, the batch temperature should be above the softening point of the resin, typically above 120 °C in the mixer chamber; full dispersion is promoted at dump temperatures of 145–160 °C. On a two-roll mill, the flakes should be sheeted into the rolling bank after filler incorporation rather than dusted onto cold polymer, because below 105 °C the flakes may remain as discrete domains and create surface defects in extruded profiles. In an intermeshing internal mixer with ram pressure of 0.5 MPa and fill factor 0.72–0.78, the resin tends to reduce power draw after the first minute of incorporation as the molten oligomer coats filler aggregates and lowers internal friction. However, if the resin is added too early in the mixing sequence, it can coat the elastomer before filler wetting is complete and increase the time to reach dispersion. For silica-filled SBR/BR compounds, the resin may compete with the silane coupling agent for the filler surface when both are added in the same pass; the usual sequence is silane first, then filler, then resin after the silanization reaction has initiated at 140 °C or above. Processors should verify by measuring bound rubber and Payne effect strain sweep under ISO 4664-1 or ASTM D5992.
In tire tread formulations, the effect of the resin is not limited to processing. Dynamic mechanical analysis of cured compounds at 10 Hz reveals that Kristalex 3115LV moves the glass transition of the SBR phase toward higher temperatures, increasing tan δ at 0 °C and often increasing tan δ at 60 °C. The first response is correlated with wet grip indicators, while the second degrades the laboratory rolling resistance indicator. A loading of 5 phr in a silica-filled passenger tire tread containing high-vinyl SBR is commonly sufficient to shift the loss tangent peak by a few degrees Celsius; the precise shift depends on vinyl content of the SBR, silane dosage, and degree of filler dispersion. Compounds using this resin should therefore be evaluated over a temperature sweep from −40 °C to 80 °C and a frequency sweep from 0.1 Hz to 100 Hz to separate the time-temperature response. Published data for this specific configuration is limited, and the magnitude of the trade-off should be measured for each compound rather than transferred from single-point literature values.
Sulfur-cured compounds containing Kristalex 3115LV do not convert the resin into a reactive coagent. However, because the resin dissolves sulfur and accelerators and lowers compound viscosity, it changes the apparent vulcanization kinetics measured by ASTM D5289 or ISO 6502. Minimum torque usually decreases with increasing resin loading, while ts1 and t90 may shift slightly due to dilution and solubility of curatives. In an EV cure system with low sulfur and high accelerator loading, polar aromatic oligomers can modify the equilibrium distribution of accelerator between rubber and filler; this may raise or lower scorch time. Therefore, cure-rheometer data on every new compound is required. In peroxide-cured elastomers, the resin can participate in hydrogen abstraction and reduce crosslink density; if use is considered, the resin should be tested in a peroxide-grade formulation at 1–3 phr before production, and residual volatile content should be minimized to avoid gas evolution during hot-air or autoclave curing.
A comparison with a partially hydrogenated C5 aliphatic tackifier of similar softening point shows that Kristalex 3115LV is more aromatic and more polar. In a standard sulfur-cured SBR/BR gum compound, phr-for-phr substitution alters curing characteristics and physical properties differently than an aliphatic control. The aromatic resin tends to reduce Mooney viscosity more at equal loading and produces a larger increase in compound glass transition temperature. This can increase wet grip and adhesion to polar substrates, but it can reduce low-temperature flexibility and may require reformulation of the plasticizer package. When compared with rosin esters, the hydrocarbon resin does not introduce carboxylic acid functionality and therefore shows less interaction with zinc oxide during storage; this can improve shelf stability in uncured rubber compounds and reduce accelerator adsorption in dry systems. Against C9 aromatic resins, Kristalex 3115LV has lower Gardner color and lower volatile content, but the cost-benefit comparison is relevant only when color and volatility are functional requirements.
With carbon black-filled compounds, the resin reduces compound viscosity and may permit higher filler loading without exceeding processing limits. In N330-filled natural rubber truck tread compounds, addition levels of 4–8 phr have been used to improve tack and maintain extrusion speed; the actual response depends on carbon black structure and oil level. Mooney viscosity measured by ASTM D1646 at ML(1+4) 100 °C should be recorded to track resin lot consistency. In mineral-filled EPDM profiles, the resin assists in wetting of calcium carbonate and calcined clay, reducing the need for paraffinic process oil and producing a smoother extrudate. However, the resin cannot replace a silane-treated mineral filler when tensile and tear requirements are severe. Tensile strength should be verified by ASTM D412 or ISO 37, tear strength by ASTM D624 or ISO 34-1, and compression set by ASTM D395 or ISO 815-1 after any material substitution.
In compounding practice, compatibility is evaluated by measuring the glass transition of a binary blend or by observing haze in a pressed film. In nonpolar elastomers such as natural rubber and high-cis BR, compatibility is generally sufficient for loadings below 15 phr; in nitrile rubber, the polarity mismatch can produce a separate phase at moderate loadings and should be investigated before production. The threshold for phase separation in NBR is not defined by the softening point but by the acrylonitrile content of the elastomer; higher ACN content increases polarity and reduces miscibility with aromatic hydrocarbon resins. The resulting phase structure can be detected as a broadening or splitting of the tan δ peak in dynamic mechanical analysis at 1 Hz under ISO 4664-1.
Green strength and building tack are influenced by resin loading and molecular weight. In uncured rubber compounds, the resin softens the matrix at processing temperatures but raises the glass transition and can increase room-temperature stiffness at higher loadings. This increases green strength in sheeted compounds, but it can also reduce drape and conformability in hand-built articles. Building tack is often measured with a probe tack test or a rolling-drum tack tester; the result depends on compound formulation, surface contamination, and storage time. Hydrocarbon resins generally provide lower building tack than rosin esters or terpene phenolics, but their lower color and better thermal stability are functional advantages in light-colored or high-temperature service products. Published data for this specific configuration is limited, so compound tack should be verified under plant storage conditions rather than predicted from generic resin chemistry.
The low-volatility designation is relevant in continuous vulcanization and hot-air curing lines where volatile organic compounds create porosity and smoke. Storage stability is influenced by pastillated form; the resin should be kept below 40 °C in a dry area to avoid blocking. Bags opened under high humidity should be consumed or re-sealed; if surface condensation is observed, warm-air drying at 50–60 °C for 2–4 h is sufficient. The material is not hygroscopic, and moisture absorption is primarily a surface phenomenon. Handling should follow general dust-control practices for organic solids, and equipment should be cleaned with warm mineral spirits or similar solvents after shutdown.
In injection molding of cured rubber, the resin lowers compound viscosity and improves cavity filling at high shear rates. Processors should monitor injection screw recovery time and barrel temperature when adding resin to an existing compound because the reduced viscosity can change back pressure and plastication behavior. Mold release behavior is generally unaffected, but if the resin level is increased beyond 10 phr, the uncured compound may retain more heat and require adjustment of cure time to prevent reversion or overcure. Capillary rheometry data at 100 s−1 and 1,000 s−1 are useful for predicting injection-molding flow; these should be generated according to ISO 11443 or a comparable high-pressure capillary rheometer method for rubber compounds.
Thermal stability in rubber service is governed by the resin’s aromatic structure and low volatile content. In hot-air aging tests under ASTM D573 or ISO 188, compounds containing the resin may show lower mass loss than those containing rosin ester tackifiers because the hydrocarbon backbone does not readily volatilize or degrade under typical rubber aging conditions. However, the resin can increase the glass transition temperature sufficiently to affect low-temperature properties after fluid immersion; therefore, low-temperature retraction and brittleness tests such as ASTM D1329 or ISO 812 should be used when service temperatures are below −20 °C.
Adhesion to reinforcing textiles and metal substrates is also modified. The resin changes the wetting behavior of the rubber compound during calendering and can improve mechanical interlocking with fabrics by reducing compound viscosity and increasing tack. In brass-coated steel cord compounds used in radial tires, hydrocarbon resin should be evaluated for its effect on adhesion retention after salt-water aging because polar aromatic species may interact with the adhesion-promoting resin system and change the cure profile at the rubber-metal interface. Adhesion force is measured by ASTM D2229 or ISO 5603 after cure and after aging; the result should be monitored for any lot-to-lot variation in resin softening point.
Regulatory acceptance depends on the end-use. For industrial rubber goods, compliance with REACH registration requirements is mandatory for EU imports; the supplier safety data sheet identifies the registered tonnage band and any restrictions. For food-contact rubber articles, the end-use composition must be tested under the applicable national or regional standard, such as FDA 21 CFR 177.2600 for rubber articles intended for repeated use, and the resin is not automatically approved for direct food contact. The product should be evaluated for residual monomer and oligomer migration against the specific packaging or food-contact regulation before commercial use. In electrical or electronic applications, RoHS compliance is managed at the finished article level, but the resin itself is halogen-free and does not contain lead, cadmium, mercury, hexavalent chromium, PBB, or PBDE as intentionally added substances.
