Asahi Kasei Tuftec™ SEBS M1913
- Product Name: Asahi Kasei Tuftec™ SEBS M1913
- Factroy Site: Yinchuan, Ningxia, China
- Price Inquiry: sales8@ascent-chem.com
- Manufacturer: Ascent Petrochem Holdings Co., Limited
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- Asahi Kasei Tuftec™ SEBS M1913 is typically used in formulations when adhesion to polar substrates and impact strength and melt processing temperature and moisture content must be controlled within specific ranges.
| HS Code | 546984 |
| Product Name | Asahi Kasei Tuftec™ SEBS M1913 |
| Manufacturer | Asahi Kasei Corporation |
| Brand | Tuftec™ |
| Grade | M1913 |
| Polymer Type | SEBS (hydrogenated styrene-butadiene-styrene block copolymer) |
| Modification | Maleic anhydride grafted |
| Appearance | White to off-white pellets |
| Form | Pellets |
| Styrene Content | Approximately 30 wt% |
| Density | Approximately 0.91 g/cm³ |
| Melt Flow Rate | Approximately 5 g/10 min (230°C/2.16 kg) |
| Shore A Hardness | Approximately 60 |
| Tensile Strength | Approximately 20 MPa |
| Elongation At Break | Approximately 500% |
| 100 Modulus | Approximately 2.5 MPa |
As an accredited Asahi Kasei Tuftec™ SEBS M1913 factory, we enforce strict quality protocols—every batch undergoes rigorous testing to ensure consistent efficacy and safety standards.
| Packing | Tuftec™ SEBS M1913 is supplied in 25 kg polyethylene-lined paper bags, typically 40 bags (1,000 kg) per pallet. |
| Container Loading (20′ FCL) | A 20-foot FCL container loaded with Asahi Kasei Tuftec™ SEBS M1913, palletized bags, evenly distributed and secured for export shipment. |
| Shipping | Asahi Kasei Tuftec™ SEBS M1913 is a non-hazardous thermoplastic elastomer supplied as pellets. Ship in clean, dry, sealed bags or containers at ambient temperature, away from moisture, direct sunlight, and heat. No special dangerous-goods classification; follow local regulations and avoid contamination during storage and transport. |
| Storage | Store Asahi Kasei Tuftec™ SEBS M1913 in a cool, dry, well-ventilated area away from direct sunlight, heat sources, moisture, and oxidizing agents. Keep it in original, tightly sealed packaging to prevent contamination and moisture pickup. Avoid prolonged UV exposure and high temperatures, and follow the SDS and local regulations. |
| Shelf Life | Typically 24 months in original unopened packaging, stored cool, dry, and away from direct sunlight. |
Polypropylene-rich thermoplastic elastomer compounds for instrument panel skins and door trim inserts are produced by introducing Asahi Kasei Tuftec™ M1913 at 25–45 phr into a co-rotating twin-screw extruder with an L/D ratio of 40:1; the polypropylene homopolymer phase is fed through the main throat while the SEBS pellets are metered downstream into the melt to limit the time–temperature history of the styrenic end blocks. Barrel temperatures are held at 180–220 °C, and the melt temperature is capped at 230 °C because prolonged residence above that threshold causes end-block domain coalescence and a measurable loss in strain recovery. On a 40 mm machine running 250–350 kg/h, die pressure and specific mechanical energy input increase as the M1913 loading is raised from 25 phr to 45 phr, reflecting the physical crosslink network imparted by the styrene end-block content. Surface hardness drops along a continuous curve from the polypropylene base value of approximately 68 Shore D toward 52–58 Shore D at 25 phr and 40–50 Shore D at 45 phr when tested per ISO 868:2003. Tensile properties measured on Type 5A dumbbells per ISO 37:2017 remain in the 12–16 MPa range at the lower SEBS addition and move toward 6–9 MPa when the elastomer fraction reaches 45 phr without process oil; elongation at break generally exceeds 300% across this window. Scratch resistance is evaluated against OEM methods such as VW PV3952, and interior fogging is assessed gravimetrically after 100 °C/16 h per DIN 75201:2021.
| Property | Standard | Condition or measured range |
| Hardness | ISO 868:2003 | 15 s reading, Shore A/D |
| Tensile strength and elongation | ISO 37:2017 | Type 5A, 500 mm/min |
| Fogging | DIN 75201:2021 | 100 °C/16 h, gravimetric |
| VOC and FOG emission | VDA 278:2011 | 90 °C/30 min VOC, 120 °C/60 min FOG |
| Odor | VDA 270:2018 | 80 °C/2 h, rating ≤3 |
| Flammability | ISO 3795:1989 | Burn rate < 100 mm/min |
What Limits Oil Extension in Low-Hardness Wire and Cable Jacketing Compounds?
In halogen-free cable jacket compounds for robotics leads and electric vehicle charging cables, M1913 is blended with a polypropylene random copolymer at 10–30 phr and a paraffinic white oil at 60–120 phr. The upper oil level is governed by the migration equilibrium between the oil and the styrene end-block domains: above 100 phr, free oil accumulates at the interface with magnesium hydroxide filler particles, and tensile strength measured per IEC 60811-501 can fall below 6 MPa for a compound containing 80 phr filler. The same compound often shows elongation at break values above 400% before hot-air aging at 110 °C/168 h, but after aging the tensile retention is frequently 70–85% when the primary antioxidant is a hindered phenol at 0.3 phr combined with a phosphite at 0.2 phr. Compounding is performed on a co-rotating twin-screw extruder with 28:1 L/D, using low-shear distributive mixing elements because the hydrogenated midblock is already saturated and excessive shear causes local melt temperatures above 240 °C, where chain scission can occur at residual unsaturation sites. Cable extrusion on a single-screw machine with 24:1 L/D and a barrier screw is run at 150–190 °C in the feed zones and 190–210 °C at the die; the melt pressure in the head is kept below 300 bar to avoid melt fracture. Finished jackets are evaluated for low-temperature impact at -40 °C per IEC 60811-506, and the elongation at low temperature normally exceeds 200% when the oil does not exceed 80 phr. A separate halogen-emission verification under IEC 60754-1 and pH measurement under IEC 60754-2 is required for low-smoke zero-halogen grades. Published data for the exact M1913 electric vehicle charging cable jacket formulation is limited; the window above is drawn from commercial halogen-free jacket practice and should be confirmed on a pilot line before serial production.
Soft-Touch Grips and Tool Overmolding: Adhesion Layer Composition at the Nylon Bond Line
M1913 does not contain grafted maleic anhydride functionality; therefore a two-shot overmolded tool grip on a polyamide 6 or 66 substrate requires either a compatibilized tie-layer or a melt blend containing 10–20 wt% of maleic anhydride–functionalized SEBS. The functionalized fraction migrates to the nylon interface during the second shot and forms covalent bridges, while the unmodified M1913 maintains the bulk Shore A 55–70 hardness and the slow stress-relaxation needed for a non-slip surface. Bond strength is evaluated by a 180° peel test on injection-molded plaques per ASTM D903-98; a compound without functionalized SEBS commonly fails at the interface below 1.5 N/mm, while the 10–20 wt% functionalized blend often produces peel forces of 4–8 N/mm with cohesive failure within the TPE layer. The injection molding window is constrained by the crystallization characteristics of the polyamide and the viscosity ratio between the two melts. The first shot is run with a mold temperature of 80–90 °C for PA66, a melt temperature of 260–280 °C, and a hold pressure sufficient to reach 95–98% mold fill by weight; the second shot is injected at 200–230 °C to avoid thermal degradation of the M1913 styrene domains while ensuring that the melt front remains above the PA substrate recrystallization temperature. Injection speed is set between 40–80 mm/s, and pack pressure is kept below 60 bar. Amine-based release agents and moisture above 0.15% in the nylon are incompatible with robust overmolding because primary amino groups can compete for the maleic anhydride graft and create low-molecular-weight imide products at the bondline.
Pressure-Sensitive Hot-Melt Adhesives—Tackifier Loading Window and Shear Reservoir Stability
Hot-melt pressure-sensitive adhesives based on M1913 require a hydrogenated hydrocarbon tackifier because the saturated ethylene-butylene midblock is miscible with low-polarity rosin ester only within a limited range; incorrect tackifier selection causes visible phase separation in the molten state and a loss of loop tack. A base formulation of 100 phr M1913, 150–300 phr hydrogenated hydrocarbon resin with a ring-and-ball softening point of 120–140 °C, and 0–80 phr naphthenic or paraffinic oil is coated through a slot die at 170–190 °C. Below 150 phr tackifier, the 180° peel on stainless steel measured per PSTC-101 is generally below 5 N/25 mm, while at 250 phr the peel values may reach 10–15 N/25 mm but cohesive failure becomes the limiting mode under 1 kg shear load per PSTC-107. The shear adhesion failure temperature, run per ASTM D4498-07 on a 25 mm × 25 mm overlap specimen with a 500 g load, decreases as tackifier loading increases because the resin partially plasticizes the styrene end-block glass transition; formulations at 300 phr resin routinely lose 15–25 °C of SAFT relative to a 150 phr formulation. Viscosity at 180 °C is governed by the high-molecular-weight SEBS backbone; without oil, the shear rate at 100 s−1 can produce viscosities above 30,000 mPa·s, whereas an addition of 40–80 phr oil brings the melt into the 8,000–15,000 mPa·s coating window. The saturated midblock gives the adhesive a lower thermo-oxidative discoloration rate than SIS or SBS systems, but a stabilizer package of 0.5 phr hindered phenol and 0.5 phr phosphite is still added prior to high-temperature slot-die coating.
In foamed footwear midsole manufacturing, a physical foam system is prepared from 100 phr M1913, 20–50 phr EVA with a vinyl acetate content of 18–28%, and 0.5–1.5 phr azodicarbonamide as chemical blowing agent. The compound is processed on a counter-rotating twin-screw extruder with a 32:1 L/D at 160–190 °C, and the melt is pelletized by a water-cooled die-face cutter into foamable beads. The EVA phase reduces the foam density, but the M1913 phase increases the elastic recovery of the cell walls after repeated compression; compression set measured at 50% strain for 6 h at 50 °C per ISO 1856:2018 is frequently 20–35% for a foam with a density of 0.20–0.30 g/cm³, compared with 40–55% for a matching EVA-only foam at the same density. Rebound resilience measured per ISO 8307:2018 increases by 5–10 percentage points when M1913 replaces an equivalent SBS or EVA fraction. During foam expansion, the styrene end-block network of M1913 limits gas loss from the blowing agent; the nucleating cell size is controlled by the ADC decomposition temperature and the melting endotherm of the EVA phase. Blowing-agent decomposition is initiated at 170–190 °C, and the die temperature is held below 200 °C to avoid over-decomposition that produces surface blowholes and collapse in the calibration unit. Peroxide addition, when used, is primarily for the EVA phase rather than for the styrenic endblock network; levels above 0.8 phr can produce odor and scorch during pelletizing. Final midsoles and insoles are held at 23 °C/50% RH for at least 24 h before dimensional verification, because foam recovery continues during the first hours after cooling.
When Medical Tubing Requires USP Class VI and ISO 10993-5 Extraction Data
Medical-grade tubing from M1913 is extruded from a blend containing 100 phr SEBS, 10–30 phr polypropylene homopolymer with an MFI of 3–8 g/10 min, and 0–10 phr paraffinic white oil; the compound is run on a medical single-screw extruder with 24:1 L/D, vacuum venting, and a barrier screw. The barrel profile is 160–210 °C, and the melt temperature at the die is kept below 220 °C. The polypropylene raises the Shore A hardness from 50–60 for plasticized SEBS to 65–75 for the finished tubing, while maintaining kink resistance. Cytotoxicity testing is conducted per ISO 10993-5:2009 on extract obtained at 37 °C/24 h with serum-containing medium; the final compound must also satisfy systemic injection, intracutaneous reactivity, and implantation tests per USP <88> Class VI if the device is marketed in the United States. Sterilization changes the mechanical signature, and the placement of the grade in the processing window must account for that shift. Gamma irradiation at 25 kGy to 50 kGy can increase the gel fraction of the midblock and raise tensile modulus by 10–25% while lowering elongation at break; ethylene oxide sterilization at 55 °C with aeration to a residual below 0.5 ppm is preferred when maximum flexibility must be preserved. The absence of phthalate plasticizers and the saturated backbone reduce the extractable oligomer level relative to SBS, but final qualification must be run on the finished device because the PP phase and any processing aids contribute their own leachables. This grade is not indicated for implant or intravascular use without supplementary biocompatibility data.
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- Asahi Kasei Tuftec™ SEBS M1913 is manufactured under an ISO 9001 quality system and complies with relevant regulatory requirements.
- COA, SDS/MSDS, and related certificates are available upon request. For certificate requests or inquiries, contact: sales8@ascent-chem.com.
Asahi Kasei Tuftec™ M1913 is a maleic anhydride–grafted hydrogenated styrene–butadiene–styrene block copolymer supplied in pellet form. The molecular architecture consists of rigid terminal polystyrene blocks and a saturated ethylene–butylene midblock; grafted anhydride and carboxylic acid groups are present at low levels. The saturated midblock provides elastomeric recovery and thermo-oxidative stability, while the anhydride functionality permits reactive compatibilization with polar substrates. Supplier-published representative values identify a styrene content of 30 wt% and a melt mass-flow rate of 5 g/10 min at 230 °C under a 2.16 kg load in accordance with ISO 1133-1:2022. Density is reported as 0.91 g/cm³ per ISO 1183-1:2019, and Shore A hardness is reported as 67 under ISO 7619-1:2010. These values are representative of commercial production and must be verified against the current technical data sheet and certificate of analysis.
The principal uses are reactive impact modification of polyamide, polyester, and polycarbonate-based compounds, and interfacial coupling in glass-fiber-reinforced polypropylene systems. Within the Tuftec product line, M1913 differs from unmodified H-series and from non-functionalized SEBS by the presence of the anhydride group. Compared with lower-flow maleated SEBS grades, M1913 is typically selected when the melt mass-flow rate of 5 g/10 min allows distribution in polyamide matrices at moderate screw energy input. The selected grade must be matched to the matrix viscosity ratio; a low-viscosity matrix may require a higher-MFR maleated grade to avoid coarse elastomer domains, while a high-viscosity matrix may retain finer dispersions with M1913. Published data for this specific configuration is limited.
What differentiates M1913 from standard SEBS elastomers?
Standard SEBS grades have no reactive polar groups; adhesion to polyamides, polyesters, and silane-treated glass depends on dispersion and physical anchoring. M1913 contains pendant anhydride groups that can undergo ring-opening during melt compounding with terminal amines in polyamide 6 and 66 or with hydroxyl and carboxyl end groups in polyesters. This reactivity changes the blend morphology: the elastomer phase is drawn into smaller domains during co-rotating twin-screw extrusion, and the interfacial region can carry covalent linkages after a conditioning step. The resulting notched impact response is therefore less sensitive to moisture regrowth in polyamide matrices than non-reactive SEBS, although published data for this specific configuration is limited.
Compared with EPDM-g-MAH, M1913 contains no main-chain unsaturation, which reduces the rate of thermo-oxidative chain scission in hot-air aging. The saturated ethylene–butylene midblock also provides better resistance to ultraviolet degradation than unsaturated polyolefin elastomers; however, UV stabilizers are still required for exterior exposure. The terminal polystyrene blocks contribute room-temperature stiffness and high-temperature creep resistance, but they also make the product susceptible to aromatic and chlorinated solvents. These differences define the substitution window for M1913 in engineering thermoplastics.
In a twin-screw extruder, the dispersed M1913 phase is subjected to elongational flow in kneading blocks and shear flow in conveying elements. The balance between breakup and coalescence sets the final particle diameter. Reactive coupling slows coalescence because the grafted interphase forms a steric and thermodynamic barrier. This is a morphological distinction from non-reactive SEBS and is evaluated by scanning electron microscopy after selective extraction of the elastomer phase. Quantified particle-size data for M1913 in PA66 are not uniformly available in public literature; published data for this specific configuration is limited.
The melt mass-flow rate of 5 g/10 min at 230 °C is a low-load indicator of melt viscosity. It is not a direct process viscosity value. For process simulation, capillary rheometry under ISO 11443:2021 at shear rates between 100 and 1500 s−1 is more relevant. Maleated SEBS grades often exhibit shear thinning; grade selection is therefore based on viscosity ratio at the shear rate prevailing in the kneading blocks. A widely used criterion in polymer blending is a viscosity ratio near 1:1 to 4:1; above this range, dispersed-phase breakup becomes inefficient. Published data for this specific configuration is limited.
When M1913 enters a PA66 compounding line at high glass-fiber loading
Compounding with M1913 requires moisture control before and during melt processing. The anhydride ring is hydrolytically sensitive; wet pellets or hopper humidity above 60 % relative humidity can cause acid formation and reduce coupling efficiency. Supplier handling guidance commonly specifies desiccant drying at 80 °C for 4 h to a residual moisture content below 0.05 wt%. Polyamide resin should be dried to below 0.10 wt% residual moisture, and the dried materials should be transferred with dry-air conveying to prevent moisture regain. This is an operational boundary, not a storage condition after processing.
A typical production configuration uses a co-rotating, intermeshing twin-screw extruder with L/D ratio of 40:1 to 52:1. The barrel profile for PA6 compounds is often set from 180 °C in the feed zone to 240–250 °C in the mixing and die zones; PA66 compounds require melt temperatures of 260–280 °C and should not be held above 280 °C for more than 60 s because anhydride decomposition and color formation can occur. M1913 is generally fed at the main feed throat with the base resin; however, when glass-fiber loading reaches 30 wt% or higher, the maleated elastomer may be split between main feed and a downstream addition port to limit shear history. Screw configurations with two or three kneading-block zones provide the high-shear dispersion needed to reduce elastomer domain size, but excessive shear heating in tightly spaced kneading elements can raise melt temperature beyond the window.
Screw design for M1913 compounding generally uses a first kneading block after the feed zone with 30° forward or neutral kneading disks to melt the matrix, and a second kneading block after glass-fiber addition with 45° reverse elements for distributive mixing. Reverse elements increase fill factor and residence time; too much reverse shear can cause localized melt temperatures above 280 °C and should be evaluated with an extruder simulation before production. Vacuum devolatilization at −0.08 MPa is used downstream to remove residual moisture and volatile low-molecular-weight compounds. The vent port must be positioned after the reaction zone so that anhydride ring-opening products are removed before die exit. If vacuum is applied too early, maleic anhydride monomer or low-molecular-weight polar species may condense in the vent and lead to clogging.
Specific mechanical energy input is typically maintained in the range of 0.20–0.30 kWh/kg for PA6-glass systems. Melt temperature is monitored by an immersion probe at the die rather than inferred from barrel setpoints. When the measured melt temperature exceeds 270 °C, screw speed is reduced or a higher free-volume screw profile is selected. For injection molding of compounds containing M1913, barrel-temperature profiles of 230–260 °C for PA6 and 260–285 °C for PA66 are used, with back pressure of 0.5–1.0 MPa and hold pressures in the 50–80 MPa range. Mold temperatures of 60–90 °C are required for adequate crystallization and impact response. These parameters are typical production settings; each finished compound must be validated against its own rheology and part geometry.
Direct combination of M1913 with primary amine-based additives should be avoided unless the amine is intended as a reactive coupling step. Uncontrolled reaction between the amine and anhydride increases melt viscosity and can form macroscopic gel particles on barrel walls and screw flights. This is a known incompatibility boundary, and cleaning with a polyolefin purge is recommended before and after use.
In impact-modified polyamide formulations at addition levels of 5–20 wt%, low-temperature ductility is commonly evaluated with notched Izod impact per ISO 180/A or notched Charpy per ISO 179-1:2010. The ductile-to-brittle transition depends on specimen notch radius, mold temperature, and conditioning to 50 % relative humidity. Single-point impact values from different laboratories are not directly comparable because moisture content shifts the matrix yield stress. Tensile properties of the final compound are measured by ISO 527-2:2012 at 23 °C and 5 mm/min; flexural modulus by ISO 178:2019. Published data for M1913 in specific PA66-glass formulations is limited; users should generate design curves across the operating temperature range rather than rely on a single datasheet value.
When M1913 is evaluated as a coupling agent in glass-fiber-reinforced polypropylene, its function overlaps with PP-g-MAH but differs in molecular architecture. The terminal polystyrene blocks of M1913 contribute room-temperature stiffness and are absent in conventional PP-g-MAH; the saturated ethylene–butylene midblock has a lower glass-transition temperature and can improve impact at −40 °C when used at the correct loading. However, M1913 is not a drop-in replacement for PP-g-MAH in all high-heat polypropylene applications because the continuous service temperature of SEBS-based modifiers is generally lower than that of PP-g-MAH. The saturated midblock does provide resistance to chain scission in hot air and UV exposure. Comparative aging under ISO 188:2023 and ASTM G154-16 should be used to quantify fitness for exterior and under-hood components.
Maleic anhydride–grafted polyolefin elastomers based on ethylene–octene copolymers remain fully saturated and have a different endblock structure; they do not contain the physical polystyrene crosslinks of M1913. In melt processing, M1913 may display sharper solidification because the polystyrene endblock domains reassociate, resulting in better green strength in some compounds. However, the styrene domains can be plasticized by certain processing aids and colorants, so additive selection must be evaluated under dynamic mechanical analysis according to ISO 6721-1:2019. Published data for this specific configuration is limited.
Thermal stability, ultraviolet resistance, and regulatory constraints
The hydrogenated midblock of M1913 removes the main-chain unsaturation present in EPDM-g-MAH and high-vinyl polybutadiene-g-MAH modifiers. In oven aging per ISO 188:2023 at 125 °C for 168 h, unfilled SEBS compounds generally show smaller loss of elongation than EPDM-based systems, provided that an appropriate antioxidant package is present. The exact retention depends on the full formulation; no single retention value can be assigned to M1913 without specifying the antioxidant system and plaque thickness. Ultraviolet resistance is evaluated with ASTM G154-16 cycle 1 using UVA-340 lamps; unstabilized SEBS will still show surface chalking and tensile loss, and UV stabilizers are required for exterior applications.
Chemical resistance is governed by the polystyrene blocks and the saturated midblock. Aromatic and chlorinated solvents will plasticize or dissolve the polystyrene domains; strong oxidizing acids can attack the saturated backbone at elevated temperature. The anhydride functionality is also sensitive to hydrolysis in prolonged hot-water immersion. When food-contact or medical use is considered, specific migration limits under EU Regulation 10/2011 and risk assessment under ISO 10993-5 apply to the finished article, not to the raw material alone. Grade-specific compliance must be confirmed in writing from the supplier before such applications are qualified.
The following checklist summarizes the typical regulatory documentation required for industrial compounding with M1913.
| Obligation | Reference / method | Documentation required |
|---|---|---|
| REACH registration | EU Regulation (EC) No 1907/2006 | SDS and registration confirmation |
| RoHS substance restrictions | 2011/65/EU and amendment (EU) 2015/863 | Supplier declaration for lead, cadmium, mercury, hexavalent chromium, PBB, PBDE and restricted phthalates |
| Food contact suitability | EU Regulation 10/2011; overall migration limit 10 mg/dm² for plastic articles | Finished-article migration testing |
| Medical device risk assessment | ISO 10993-1:2018 | Biological evaluation plan |
Because M1913 is a modified polymer rather than a simple monoconstituent substance, the regulatory status depends on the final compounding step and the converting region. The absence of a supplier declaration for a specific application should be treated as a notice that further migration and registration review is required, not as an implied clearance.
