Dual Network Co-Crosslinked HNBR Composites with Enhanced Tribological Properties under Water Lubrication

Abstract

Water-lubricated bearings play a critical role in underwater propulsion systems but are often prone to failure due to mechanical wear and vibration, especially under high loads and prolonged friction. In response to this issue, our study introduces a novel approach: a dual network co-crosslinking strategy utilizing hydrogenated nitrile butadiene rubber (HNBR). This strategy connects the rubber network with the epoxy network through epoxidized Eucommia ulmoides gum. A comprehensive analysis was conducted to assess the resulting composite’s damping, tribological, and mechanical properties. The results show that the material has excellent mechanical, damping, and tribological properties relative to pure HNBR, with a 65.9% increase in the damping temperature domain, a 78.5% increase in tensile strength, a low coefficient of friction of 0.022, and a high resistance to abrasion of 3.87 × 10⁻⁶ mm³/Nm. The successful synthesis of HNBR-based composites via the dual network co-crosslinking strategy underscores their potential as a practical solution for improving the reliability and prolonging the service life of water-lubricated bearings.

1. Introduction

As an important component of underwater propulsion systems, water-lubricated bearings have attracted much attention in the mechanical field [1,2,3]. Compared with the traditional oil lubrication method, water-lubricated bearings have many advantages, such as safety, environmental protection, economy, and greenness, thus becoming an important direction of underwater bearing research [4,5,6,7]. However, compared with oil-lubricated bearings, water-lubricated bearings also have some disadvantages. For example, the poor load carrying capacity and low adsorption capacity of water lead to poor boundary lubrication performance [8,9,10]. Therefore, it is necessary to further improve the performance of water-lubricated bearings through technical improvement and design optimization, so as to enhance the reliability and service life of water-lubricated bearings and promote their application in non-underwater propulsion systems.

Rubber elastomers, as polymeric water lubrication materials, are effective in reducing bearing friction and wear under water lubrication conditions and have a low coefficient of friction [11,12,13]. In addition, the rubber material can absorb vibration and shock and reduce the generation of noise and vibration [14]. Among them, hydrogenated nitrile butadiene rubber (HNBR) is a product obtained by catalytic hydrogenation technology of nitrile rubber, which has higher oxidative stability, abrasion resistance, and smaller permanent compression deformation compared with traditional nitrile rubber [15,16].

When HNBR is used alone as a water-lubricated bearing, it can experience elevated temperatures under higher loads and conditions with reduced water availability or limited water film formation, which may lead to scorching and frictional failure [17]. For this reason, researchers have conducted numerous studies on HNBR water lubrication materials. Common ways to improve the friction performance include the addition of solid lubricants [18,19], microcapsules [20,21], blending [22,23], and surface modification [24,25]. Compared with pure HNBR, polymer blending is also a way to improve the performance of rubber materials. Chudzik et al. added modified epoxy diene resin to NBR and the addition of 10% unmodified resin (ED-20) resulted in the most significant reduction in friction of vulcanized NBR, with a reduction of 25% in friction [26]. Sang et al. grafted a silane coupling agent functional layer on the surface of plasma-functionalized polyamide (PA 6), the joining of PA 6 with hydrogenated nitrile butadiene rubber (HNBR) was achieved, and the heat resistance of the material was improved [27]. Zhou et al. investigated the effect of blending different fillers on the friction and wear properties, mechanical properties, and vulcanization properties of HNBR, and the UHMWPE/HNBR composites had the best friction properties with low-speed water lubrication [3]. People are committed to improving the performance of HNBR. Therefore, we believe that the introduction of high-performance polymers with good physicochemical properties can prepare composites with excellent performance.

Eucommia ulmoides gum (EUG) is a renewable natural rubber (NR) with excellent dynamic mechanical properties in a wide range of high-performance rubber materials, including tires, vibration-damping devices, and acoustic materials [28,29]. Epoxidized Eucommia ulmoides gum (EEUG) prepared by simple epoxy functionalization is effective in improving compatibility with polar ingredients. Wang et al. succeeded in improving the adhesive properties at the styrene butadiene rubber (SBR)/silicon dioxide (SiO₂) interface with mechanical properties exceeding those of other compatibilizers using epoxy dutasteride rubber as a compatibilizer [30]. Chen et al. developed an EEUG/epoxy (EP) composite coating, where the introduction of EEUG increased the crosslinking density, giving the coating excellent tensile strength and corrosion resistance [31]. Wang et al. prepared a tough biobased composite with a shape memory effect using a dynamic vulcanization technique [32]. Therefore, EEUGs enriched with epoxy groups and double bonds can effectively improve the compatibility of rubbers and polymers such as epoxy resins.

In this study, we report the development of a novel dual network co-crosslinked system that combines two networks, rubber and epoxy, by introducing epoxidized Eucommia ulmoides gum as an intermediate. We investigated the frictional properties of the material using a ring block friction and wear tester and revealed the mechanism of water lubrication in the dual network co-crosslinked system. Our results demonstrate that the introduced epoxy Eucommia ulmoides gum effectively links the separate crosslinking systems of rubber and epoxy resin and significantly improves the damping and tribological properties of the material. These findings suggest that our approach has potential applications in tribology and other engineering fields.

2. Materials and Methods

2.1. Materials

Hydrogenated nitrile butadiene rubber, LANXESS 4369, Germany, has an acrylonitrile content of 43% and a Menni viscosity (ML 1 + 4) of 97 at 100 °C. It was purchased from Meifu New Material Co., Ltd., (Suzhou, China). Eucommia ulmoides gum (EUG) was obtained from Beijing Huayan Shijia Quality Control Technology Co. (Beijing, China). Haine epoxy resin was obtained from Wuhan Lanabai Pharmaceutical & Chemical Co. (Wuhan, China) 4,4’-Methylene-bis(2-chloroaniline) (MOCA) was obtained from Anhui Xianglong Chemical Co. (Anqing, China) Stearic acid, sulfur, zinc oxide, carbon black (N220), tetramethylthiuram disulfide (TMTD), and 2-thiobenzothiazole (MBT) are all industrial grade. All chemicals, unless otherwise stated, were used without further purification.

2.2. Preparation

2.2.1. Preparation of Epoxidized Eucommia Ulmoides Gum

In the reaction vessel, 30 g of EUG was added to 600 mL of xylene with high-speed stirring at 40 °C to completely dissolve the EUG. A mixture of H₂O₂ (13.6 g) and formic acid (5.6 g) was added dropwise to the reaction vessel over a period of 2 h. The reaction was continued for 3 h. At the end of the reaction, the product was precipitated by addition of excess ethanol, then filtered, washed, and dried in a vacuum oven at 50 °C for 36 h to give EEUG.

2.2.2. Preparation of HNBR/EEUG Composites

The preparation process of the material is shown in Figure 1. HNBR and rubber additives such as zinc oxide, tetramethylthiuram disulfide (TMTD) 2-thiobenzothiazole (MBT), etc. were added to the mixer and mixed well to obtain the rubber master batch. The HNBR rubber master batch was chopped and added to a three-necked flask, and tetrahydrofuran (THF) was added at 1:10, accompanied by stirring for 12 h to dissolve it completely. EEUG was dissolved in a small amount of THF and subsequently added to the HNBR gum solution along with sulfur and MOCA with stirring for 1 h. After sufficient stirring, the solvent was placed on a far infrared graphite heating plate at 55 °C.

Table 1. Materials and formulation.

Samples (phr)	HNBR	EEUG	HER	S	MOCA	SA	ZnO	TMTD	CB220	MBT
100:0:0	100	0	0	2	0	0.8	2.5	0.65	60	0.45
100:7:0	100	7	0	2.14	2.8	0.8	2.5	0.65	60	0.45
100:7:5	100	7	5	2.14	3.6	0.8	2.5	0.65	60	0.45

lists information on the components of the material. The obtained film was alternately triangularly wrapped and rolled 6 times on an open mill. The film was vulcanized in a plate vulcanizer at 150 °C and 10 MPa for 30 min. Finally, the samples were cured at 80 °C for 3 h; 120 °C for 3 h; 150 °C for 5 h under gradient temperature increase. The mass ratios of the prepared HNBR/EEUG composites, HNBR to EEUG, were 100:3, 100:5, 100:7, 100:9, and 100:11.

2.2.3. Preparation of Dual Network Co-Crosslinked Composites

The dual network co-crosslinked composites were prepared in a similar way to the former preparation method, in which HER and HNBR were dissolved together in THF, and based on the results of the later experiments, the composite of HNBR/EEUG 100:7 was selected as the matrix, and the ratios of HNBR/HER/EEUG were 100:7:3, 100:7:5, 100:7:7, and 100:7:9.

2.3. Tribological Tests

Friction and wear tests were carried out under water lubrication conditions using the MRH-3 ring wear tester produced by Era Test Metals Inc. and schematically shown in Figure 2. The friction partner was a tin-bronze ring (ZCuSn10Zn2) with the composition shown in

Table 2. Chemical composition of ZCuSn10Zn2.

Ingredient	Cu	Sn	Zn	Pb	Ni	Fe	Mn	Sb	S
Concentration (phr)	83.65	10	2	1.5	2	0.25	0.2	0.3	0.1

. The surface of the specimen ring was ultrasonically cleaned in ethanol by grinding the specimen ring surface with 800 mesh metallographic sandpaper until smooth. At room temperature, the experimental speed was set at 140 revolutions per minute (rpm), the test force was 132 N, and the test drops were added with water on the surface of the friction subsurface. The acceleration rate of all the test drops was 9 mL/min, and the water was refilled at the end of each test. The stable friction value during the last 30 min of the experiment was taken as the average friction coefficient. The surface of the block material was wiped with anhydrous ethanol before and after friction and dried at 60 °C for 2 h. The specific wear rate (Ws, mm³/Nm) was calculated by the following relation:

$$W_S=V_S/F\ast 2\pi R\ast n\ast nt\ast t \left({\mathrm{mm}}^3/\mathrm{Nm}\right)$$

(1)

where Vs (mm³) represents the wear volume of each friction rubber block and is given in the following equation. R denotes the outer diameter of the tin bronze ring, and F, n, and t represent the normal load (N), rotational speed (rpm), and test time (min), respectively.

$$V_S=\frac{D^2}{8}t\left[2{\sin }^{-1}\frac{b}{D}-\sin \left(2{\sin }^{-1}\frac{b}{D}\right)\right] \left({\mathrm{mm}}^3\right)$$

(2)

where D (mm) is the outer diameter of the tin bronze ring and b (mm) and t (mm) are the average width of the abrasion mark and the width of the rubber block, respectively. To ensure the reliability of the experimental data, the average of three measurements is taken as the experimental data.

2.4. Characterizations

¹H NMR spectra were recorded at 25 °C on a nuclear magnetic resonance spectrometer (Bruker AVIII 400 MHz, USA). EUG and EEUG were dissolved in CDCl₃ and transferred to NMR tubes for subsequent determinations. Samples were analyzed using Fourier transform infrared spectroscopy (FT-IR, Bruker S V70). The mechanical properties of the materials were characterised by an AD-X (5000 N) universal testing machine (Shimadzu, Japan) and at least three samples were tested at a tensile speed of 500 mm/minute to obtain the average value. In order to clearly observe the micro-morphology of the material and to analyse its phase behaviour, we characterised the surface of the material using a Multimode 8 atomic force microscope (AFM) (Bruker, USA). The friction surface morphology of the material was observed by SEM, and the friction surface was sprayed with gold to increase the electrical conductivity of the material surface before testing. The contact angle (CA) of water on the surface of the material was measured on a DECCA-100 optical contact angle meter (DECCA Precision Instruments Co., Ltd., Shenzhen, China) using the sessile drop method. To obtain a more accurate value, the CA was measured randomly at three different positions on the friction surface of the sample, and then the arithmetic mean was obtained. The damping properties of the materials were characterized by DMA with the following parameters: the mode was tensile mode, the fixed frequency was 10 Hz, the temperature range was from −60 °C to 60 °C, and the temperature increase rate was 5 °C/min.

3. Results and Discussions

3.1. EEUG Characterization

Eucommia ulmoides gum, which is mainly composed of trans-isoprene, is poorly compatible with polar hydrogenated nitrile rubber because of its high degree of crystallinity and non-polar nature, and epoxy functionalization has become a simple and effective way to improve its compatibility. The successful epoxidation of dulcimer rubber is proved by the FT-IR spectra shown in Figure 3a, which shows that the peak of C=C telescopic vibration at 1665 cm⁻¹ decreases after epoxide functionalization [33], the symmetric and asymmetric vibrational absorption peaks of C-O-C are enhanced at 1263 cm⁻¹ and 870 cm⁻¹, 1665 cm⁻¹ is C=C telescopic vibration, which decreases the peak after epoxidation, and the C-O-C symmetric and asymmetric telescopic vibrational peaks are observed at 1264 cm⁻¹ and 870 cm⁻¹ [34]. In Figure 3b, the signals at 1.61, 1.98–2.09, and 5.13 ppm are attributed to CH₃, CH₂, and alkene protons, respectively, in the trans-1,4 structure. The peak at 1.29 ppm is attributed to the methyl peak of the epoxide group. The peak at 2.71 ppm is due to the proton resonance of C-O-C, which suggests that some of the double bonds on the EUG chain were successfully epoxidized [35]. Epoxidized Eucommia ulmoides gum has both C=C and epoxy bonds, which can be crosslinked by both MOCA and S at the same time, providing conditions for HNBR to “connect” with HER.

3.2. Mechanical Properties of Composite Materials

Mechanical properties have an important impact on the application of materials, and the introduction of EEUG and HER into HNBR will inevitably cause changes in its mechanical properties. For this purpose, tensile measurements were performed, and the results obtained are shown in Figure 4. The tensile strength and elongation at break of the composites increased from 278.52% and 20.41 MPa to 598.4% and 29.4 MPa, respectively, with the addition of EEUG. For rubber composites with different additions of EEUG, the elongation at break and tensile strength increased with the increase in EEUG content. This indicates that the addition of EEUG improves the mechanical properties of pure HNBR. This is due to the good compatibility between EEUG and HNBR, and the incorporation of EEUG as a physical crosslinking point increases the entanglement between molecular chain segments. With the addition of HER, a dual network co-crosslinking system was formed under the dual crosslinking of sulfur and MOCA. The maximum tensile strength of the material is 36.17 MPa, which is 78.5% higher than that of pure HNBR. This is attributed to the incorporation of HER to form a second network, and in the double crosslinking system, the chain segments of the polymers are chemically crosslinked and physically entangled, resulting in the formation of a denser structure. The hardness of the material increases at the macroscopic level.

3.3. Damping Analysis of Composites

Bearings under water lubrication conditions experience significant vibration, which is not conducive to the actual service life of the material. Therefore, studying the damping properties of composite materials for bearings in vibration damping is of great significance. The damping properties of polymers are closely related to the internal friction generated by the relative slip of the polymer molecular chains [36]. Figure 5 shows the variation of energy storage modulus (E’) and loss factor (Tanδ) with temperature for different formulations of HNBR at 10 Hz, and

Table 3. Damping properties of different composites.

HNBR/EEUG	$\mathbf{Tan}\mathit{\delta }$max	ΔT ($\mathbf{Tan}\mathit{\delta }$ > 0.3)	HNBR/EEUG /HER	$\mathbf{Tan}\mathit{\delta }$max	ΔT ($\mathbf{Tan}\mathit{\delta }$ > 0.3)
100:0	0.65	16.42	100:7	0.55	26.82
100:3	0.51	22.07	100:7:3	0.52	28.45
100:5	0.53	24.95	100:7:5	0.54	30.80
100:7	0.55	26.82	100:7:7	0.52	29.85
100:9	0.58	23.87	100:7:9	0.48	27.24
100:11	0.60	24.08	-	-	-

shows the material effect damping temperature domain. The polymer effect damping temperature range is defined as the temperature range where Tanδ exceeds 0.3. With the addition of soft EEUG, the energy storage modulus of the material decreases and is lower than that of the HNBR, but the effective damping range becomes wider. Having the largest energy storage modulus when HNBR/EEUG is 100:7, there is only a single peak in Tanδ for all the samples, which indicates that epoxidation gives good compatibility between dulcimer rubber and HNBR. With the addition of HER, the energy storage modulus gradually increases, while the loss factor is shifted to the high-temperature direction, and the maximum damping temperature domain is increased by 65.9% compared with that of pure HNBR. This phenomenon may be due to two reasons: one is that the EEUG acts as a “bridge” between HNBR and HER, and the two, through chemical crosslinking to connect the polymer after crosslinking, further reduce the polymer molecular chain of the internal rotation and lead to a further increase in the molecular chain of the internal friction, ultimately accelerating the internal energy dissipation of the polymer, which improves the damping performance of the material; second, it is caused by the greater rigidity brought by the HER five-membered nitrogen heterocycles, so the increase in the HER content leads to the enhancement of the interaction force between the two, which restricts the movement of the molecular chains (chain segments) in the free volume and leads to the increase in Tg. The high-HER component leads to the electrostatic repulsive force between the polar groups exceeding the attractive force, resulting in an increase in the intermolecular distance between the molecular chains and a decrease in the glass transition temperature.

3.4. Tribological Properties of Composites

3.4.1. Tribological Properties of HNBR/EEUG

The tribological properties of composites have a decisive influence on their service conditions. By investigating the frictional properties of HNBR and EUG at different ratios, the frictional wear curves of HNBR/EEUG composites at different ratios under water lubrication conditions are shown in Figure 6. From Figure 6a, it can be seen that the friction curves showed very different trends after the addition of EEUG. The HNBR showed an increasing and then decreasing trend at the beginning of the friction, while the friction coefficients all showed a rapid decrease after the addition of EEUG, and then they all leveled off. In the early stages of friction, pure HNBR experiences a boundary lubrication state due to the growth of the transfer film and an increase in the friction vice contact area. This leads to an initial rise followed by a subsequent decrease in the friction coefficient. HNBR/EEUG composites show a different behavior during the initial stages of sliding, where the formation of a water film leads to a rapid decrease in the surface friction coefficient from boundary lubrication to mixed lubrication [37]. With water film stabilization, the friction coefficient of the decline gradually slows down and eventually stabilizes. With the increase in EEUG content, the friction coefficient appeared to decrease and then increase. At 7%, the material’s coefficient of friction reached a minimum of 0.047, and it is exciting that the friction coefficient with the addition of EEUG is less than that of the pure HNBR. It can be concluded that the addition of EEUG is of great significance in improving the tribological properties of HNBR. The reduction in the friction coefficient is mainly attributed to the plasticizing and softening effect of EEUG on HNBR, which makes the contact area between the friction pair increase, and the larger friction surface makes the water film have a larger carrying capacity [38]. As shown in Figure 6b, the wear rate increases gradually with the addition of EEUG. The reduction in hardness makes the material more likely to adhere to the pair of surfaces under shear, which reduces the load-bearing capacity of the water film rupture, increases the coefficient of friction, and makes it more susceptible to wear [39].

To study the microscopic wear of the friction material, a scanning electron microscope was used to observe the friction surface. As shown in Figure 7a, the pure HNBR friction surface has stripping and microcracks along the friction direction, which is mainly dominated by adhesive wear. As shown in Figure 7b–f, after the addition of EEUG, the friction surface shows plow furrows, which are mainly dominated by abrasive wear, which is caused by the microcutting of the polymer by the hard tin bronze surface. With the addition of EEUG, the modulus of the material gradually decreases, which reduces the abrasion resistance of HNBR and aggravates the abrasion of the material under strong shear force.

The results show that the incorporation of EEUG effectively improves the friction properties under water lubrication conditions, and the coefficient of friction of the composites decreases by nearly two thirds relative to that of pure HNBR at an EEUG content of 7%, but the incorporation of EEUG reduces the wear resistance of pure HNBR. Therefore, we propose a dual network co-crosslinking system based on the addition of HNBR/EEUG 100:7 with the addition of polar HER and expect these dual network co-crosslinked composites to have excellent tribological properties.

3.4.2. Frictional Properties of Dual Network Co-Crosslinked Composites

The curves of the friction coefficients of different dual network co-crosslinked systems as a function of test time and the effect of HER content on the average friction coefficients and wear rates are shown in Figure 8. Figure 8a shows images of the friction coefficient with time for dual network co-crosslinked systems with different HER contents. In the early stage of friction, with the addition of HER content, the friction time is gradually shortened, and the fluctuation of the friction coefficient decreases due to the better damping property of the material. The friction coefficient decreases rapidly and stabilizes, which is attributed to the uniform multiphase structure of the matrix material, and the friction coefficient decreases to 0.022. With the addition of HER to form a double network co-crosslinking system, the hardness and modulus of the material gradually increased, greatly improving the wear resistance of the material. The coefficient of friction is reduced, and at the same time, there is a better improvement in the wear resistance, and the wear rate is reduced to 3.87 × 10⁻⁶ mm³/Nm. There is a significant reduction in the coefficient of friction and wear rate of the dual network co-crosslinked composites in Figure 8 relative to Figure 6. The enhanced friction performance is mainly attributed to the following two aspects. First, the synergistic effect of HER incorporation into the gradually formed dual network enables the water lubrication process from boundary lubrication to mixing lubrication to progress quickly, resulting in smaller fluctuations in the material friction coefficient. Second, the gradual formation of the second network leads to a gradual increase in the modulus and hardness of the composite material, smaller plastic deformation makes the material more resistant to shear, and the boundary lubrication performance of the material gradually increases, making the material more wear resistant.

Figure 9 shows SEM images of the friction surfaces of the dual network co-crosslinked composites at different mass ratios. As shown in Figure 9b–d, a small number of grooves gradually disappeared after the formation of the dual network co-crosslinking system, and the friction surface became flatter, mainly dominated by slight plastic deformation. The flat friction surface makes the water film stronger and more complete, which is more conducive to the separation of the water film from the friction subsurface, while the material friction surface produces only a small amount of wear debris [40]. As Figure 9c shows, the friction surface is flat with only a small amount of abrasive debris, which is mainly dominated by slight abrasive wear [41]. All the above results indicate that the dual network co-crosslinked composites possess a low coefficient of friction and wear rate.

3.5. Microscopic Morphology Analysis

The phase morphology of the friction surface was examined using AFM in tap mode. The surface roughness and surface properties of the composite material are critical for the friction properties of the material. The AFM image is 256 × 256 pixels with a scanning range of 5 μm × 5 μm. The AFM image of the material is shown in Figure 10. From the comparison of the AFM morphology of the friction surface after friction with the phase image, Figure 10(a1–c1) show that in the material surface images, the material rms roughness Rq is 9.85 nm, 8.01 nm, and 7.92 nm in order, and the roughness decreases in order, which corresponds to the friction coefficient of the material [42]. The smoother surface may be an important factor in the formation of a stable water film during the friction process, avoiding large protrusions that can pierce the water film and weaken the lubrication effect. The low roughness reduces the mutual resistance between the friction partners and thus improves the boundary lubrication, resulting in a material with a lower coefficient of friction and wear rate [43]. The corresponding phase diagrams show that the latter has changed considerably from pure HNBR, as shown in Figure 10(a2–c2), where agglomeration of carbon black particles is unavoidable in pure HNBR, and the addition of EEUG improves the compatibility of carbon black. No obvious phase separation was observed in the phase diagrams of the latter two, which proves that the components of the prepared materials have good compatibility.

3.6. Water Contact Angle

The water contact angle was tested on the friction surface of the samples. As shown in Figure 11, the water contact angle decreases sequentially, and the water contact angle of the dual network co-crosslinked system decreases by 22.8° with respect to the pure HNBR. The hydrophilicity of the material improves due to the introduction of both EEUG and HER with hydrophilic groups [44]. The hydrophilic surface facilitates the formation of a water film during friction, which can better separate the friction partners, thus reducing the coefficient of friction and wear rate.

3.7. Long-Term Wear Test

To understand the wear resistance of rubber matrix composites co-crosslinked with dual networks, long-term friction and wear experiments were carried out, and the experimental conditions were set at a 132 N load and 140 rpm, and the experimental time was 12 h. As shown in Figure 12a, the double network co-crosslinked rubber matrix composites have smoother surfaces and lower friction coefficients under prolonged friction, and the SEM friction surface images are shown in Figure 12b–d. HNBR-7-5 has the smoothest and flattest friction surface, which is direct proof of the material’s good abrasion resistance. Overall, HNBR-7-5 still has good tribological properties after the long-term wear test.

4. Conclusions

In this paper, a dual network co-crosslinked rubber matrix composite is developed. By using epoxidized Eucommia ulmoides gum as a “bridge” between HNBR and HER, the two are chemically crosslinked. Then, the mechanical properties, damping properties, friction properties under water lubrication conditions, and microscopic morphology of the composites were systematically investigated. Atomic force microscopy results show that the dual network co-crosslinked composites have a uniform phase morphology, friction properties, and damping properties and a flatter friction surface. The frictional properties of the dual network co-crosslinked composites were significantly improved with the formation of dual networks, the friction coefficients of COF and Ws were reduced to 0.022, and the wear rate was reduced to 3.87 × 10⁻⁶ mm³/Nm in HNBR/EEUG/HER 100:7:5. The effective damping temperature domain of the composites is increased by 87.6% compared with that of pure HNBR. New ideas and practices are provided for the design of composites with good water lubrication and vibration-damping properties in the field of underwater propulsion.