Tin-based babbitt alloy and its preparation method and application

Abstract

The present invention provides a tin-based babbitt alloy, its preparation method, and application, relating to the technical field of babbitt alloys. Specifically, the tin-based babbitt alloy comprises the following elemental components, measured by weight percentage: Sb 5% to 15%, Cu 2% to 10%, Ni 0.05% to 2%, Co 0.05% to 3%, Fe 0.01% to 0.3%, La 0.01% to 0.5%, Ce 0.01% to 0.6%, Yb 0.01% to 0.5%, and the balance Sn. By improving the composition of the tin-based babbitt alloy, the present invention reduces the wire breakage rate during the production process, improves processing efficiency, and avoids limitations in additive manufacturing processes caused by problems such as difficulty in drawing alloy wire and frequent wire breakage. The present invention also provides a preparation method and application of the tin-based babbitt alloy, which has broad application prospects.

Description

Technical Field

[0001] The present invention relates to the technical field of babbitt alloys, and in particular to a tin-based babbitt alloy and a preparation method and application thereof. Background Art

[0002] Babbitt metal is a low-melting-point bearing alloy consisting of a hard particle phase distributed on a soft matrix. It is generally divided into three series: tin-based, lead-based, and cadmium-based. Tin-based babbitt metal is widely used in the production and repair of bearing shells due to its excellent friction reduction, compliance, and anti-seizure properties. Traditionally, the wear-resistant babbitt metal layer of bearings is produced using gravity casting and centrifugal casting. Gravity casting is a more mature process, but it suffers from low bonding strength between the babbitt metal layer and the steel matrix, severe structural segregation under gravity, a complex process flow, and high material and energy consumption. Centrifugal casting uses centrifugal force to pour liquid alloy onto the bearing substrate, improving bonding strength. While this improves structural segregation, it still doesn't fundamentally address the problem of coarse microstructure. Furthermore, due to equipment limitations, centrifuge casting cannot be used for large bearing shells. Currently, gravity casting and centrifugal casting are primarily used in applications such as steam turbines where bonding strength requirements are low.

[0003] Additive Manufacturing (AM) is a technology that uses a gradual accumulation of materials to manufacture physical parts. It has also been applied in the field of Babbitt alloy bearings. The process is based on three-dimensional model data. A robot drives the welding heat source to manufacture the workpiece by accumulating materials. For workpieces with complex shapes (such as multiple alloy surfaces), continuous operation can be performed on one device and in one process, significantly reducing processing efficiency. Therefore, the preparation of bearings by additive manufacturing technology has a shorter process flow than the preparation of bearings by gravity casting or centrifugal casting, and can also solve many technical defects of the above two in the casting process. On the one hand, additive manufacturing solves the problem of low bonding strength between Babbitt alloy and iron base. On the other hand, the bearing structure obtained by additive manufacturing is very uniform and has high bonding strength, while solving the problem of tin bias in traditional casting.

[0004] Currently, several leading domestic bearing manufacturers are actively introducing additive manufacturing (AM) technology to replace casting. In the manufacturing of bearings using tin-based babbitt alloy as a friction-reducing material, the use of AM instead of casting aligns with the trend toward high efficiency, high precision, high reliability, and long life for bearings, offering a broad range of applications. However, the current babbitt wire used in AM is difficult to draw and frequently breaks, hindering its application in AM.

[0005] In view of this, the present invention is proposed. Summary of the Invention

[0006] The first purpose of the present invention is to provide a tin-based babbitt alloy to solve the technical defects of conventional babbitt alloys that are prone to difficulty in drawing alloy wires and frequent wire breakage when used in additive manufacturing processes. The present invention improves the components of the tin-based babbitt alloy, reduces the wire breakage rate in the production process, improves processing efficiency, and to a certain extent avoids the limitations on the selection of additive manufacturing processes caused by problems with the wire used in additive manufacturing.

[0007] The second object of the present invention is to provide a method for preparing the tin-based babbitt alloy, which is simple and easy to implement, has low mechanical cost, and is suitable for industrial production.

[0008] The third object of the present invention is to provide a use of the tin-based babbitt alloy in the field of preparing bearing bushes.

[0009] In order to achieve the above-mentioned purpose of the present invention, the following technical solutions are adopted:

[0010] A tin-based babbitt alloy comprises the following elemental components by weight: 5% to 15% Sb, 2% to 10% Cu, 0.05% to 2% Ni, 0.05% to 3% Co, 0.01% to 0.3% Fe, 0.01% to 0.5% La, 0.01% to 0.6% Ce, 0.01% to 0.5% Yb, and the balance Sn.

[0011] The preparation method of the tin-based babbitt alloy comprises the following steps:

[0012] S1. Prepare the raw material components according to weight ratio; the raw material components include Sn, Sb, Cu, Ni, Co, Fe, Cu80La8Ce12 and Sn60Yb40;

[0013] S2, placing all raw material components except Sn and part of tin in a container for smelting to obtain a first molten liquid; after the smelting is completed, adding the remaining tin to the first molten liquid, and carrying out a heat-insulating reaction to obtain a second molten liquid;

[0014] S3, adding a refining agent to the second molten liquid, mixing thoroughly and then allowing to stand; and obtaining a tin-based babbitt alloy after casting.

[0015] The tin-based babbitt alloy, or the tin-based babbitt alloy prepared by the preparation method of the tin-based babbitt alloy, is used in the field of preparing bearings, and the bearings are prepared by additive manufacturing technology.

[0016] Compared with the prior art, the beneficial effects of the present invention are as follows: the present invention adds trace amounts of high-melting-point elements Co, Ni, Fe and rare earth elements La, Ce, and Yb to the tin-based babbitt alloy; wherein the Co and Ni elements can react with the Sn element in the alloy matrix to generate Co2Sn and Ni3Sn4 compounds to inhibit the formation of interfacial brittle phases FeSn and FeSn2, thereby improving the babbitt alloy / steel interface strength; at the same time, the rare earth elements can refine the alloy matrix structure, improve the alloy's plastic toughness, tensile strength and solution surface activity, inhibit ingot oxidation, and improve the wire drawing performance. BRIEF DESCRIPTION OF THE DRAWINGS

[0017] In order to more clearly illustrate the specific embodiments of the present invention or the technical solutions in the prior art, the following briefly introduces the drawings required for use in the specific embodiments or the description of the prior art. Obviously, the drawings described below are some embodiments of the present invention. For ordinary technicians in this field, other drawings can be obtained based on these drawings without paying any creative work.

[0018] Figure 1 This is an electron microscope image of the metallographic structure of Example 1 of the present invention;

[0019] Figure 2 This is an electron microscope image of the metallographic structure of Example 2 of the present invention;

[0020] Figure 3 This is an electron microscope image of the metallographic structure of Example 3 of the present invention;

[0021] Figure 4 This is an electron microscope image of the metallographic structure of Example 4 of the present invention;

[0022] Figure 5 This is an electron microscope image of the metallographic structure of Comparative Example 1 of the present invention;

[0023] Figure 6 This is a comparison diagram of the ingot surface of Example 1 of the present invention and Comparative Example 1;

[0024] Figure 7 This is a physical comparison diagram of Example 1 of the present invention and Comparative Example 1. DETAILED DESCRIPTION

[0025] The technical scheme of the present invention will be clearly and completely described below in conjunction with the accompanying drawings and specific embodiments, but it will be understood by those skilled in the art that the following described embodiments are part of embodiments of the present invention, rather than all embodiments, and are only used to illustrate the present invention, and should not be considered as limiting the scope of the present invention. Based on the embodiments in the present invention, all other embodiments obtained by those of ordinary skill in the art without making creative work are within the scope of protection of the present invention. Those who do not specify specific conditions in the embodiments are carried out according to normal conditions or the conditions recommended by the manufacturer. Those whose reagents or instruments are not specified by the manufacturer are conventional products that can be purchased commercially.

[0026] The Babbitt alloy wires commonly used in current additive manufacturing are mainly divided into SnSb8Cu4 or SnSb11Cu6, and the performance of SnSb11Cu6 is better than SnSb8Cu4. The Sb and Cu content in SnSb8Cu4 is not high, and it is easy to reduce the diameter during the extrusion and drawing process; the cast structure of SnSb11Cu6 is rich in coarse hard phases and has poor flexibility. In addition, during the casting process, the surface of the melt turns yellow and is easily oxidized, and oxidation inclusions will exist during the drawing process, which ultimately leads to frequent wire breakage and poor wire drawing performance. The present invention can achieve improvements to the above-mentioned technical defects by improving the elemental composition and ratio of tin-based Babbitt alloy and limiting the preparation process flow. The present invention is carried out through the following specific implementation methods:

[0027] A tin-based babbitt alloy comprises the following elemental components by weight: 5% to 15% Sb, 2% to 10% Cu, 0.05% to 2% Ni, 0.05% to 3% Co, 0.01% to 0.3% Fe, 0.01% to 0.5% La, 0.01% to 0.6% Ce, 0.01% to 0.5% Yb, and the balance Sn.

[0028] As a preferred embodiment, the tin-based babbitt alloy includes the following elemental components by weight percentage: Sn 75% to 92%, Sb 5.5% to 14%, Cu 2.5% to 9%, Ni 0.05% to 1.5%, Co 0.05% to 2%, Fe 0.01% to 0.2%, La 0.01% to 0.4%, Ce 0.01% to 0.5% and Yb 0.01% to 0.4%.

[0029] As a more preferred embodiment, the tin-based babbitt alloy includes the following elemental components by weight percentage: Sn 75.7% to 90.86%, Sb 6% to 13%, Cu 3% to 8%, Ni 0.05% to 1%, Co 0.05% to 1.5%, Fe 0.01% to 0.1%, La 0.01% to 0.2%, Ce 0.01% to 0.3% and Yb 0.01% to 0.2%.

[0030] As an optional embodiment, the weight percentages of the constituent elements of the tin-based babbitt alloy include but are not limited to the following specific values: Sn 75.7%, 76%, 80%, 82%, 84%, 86%, 88%, 90%, 90.86%; Sb 6%, 7%, 8%, 9%, 10%, 11%, 12%, 13%; Cu 3%, 4%, 5%, 6%, 7%, 8%; Ni 0.05%, 0.1%, 0.2%, 0.3%, 0.4%, 0.5%, 0.6%, 0.7%, 0.8%, 0.9%, 1%; Co 0.05%, 0.1%, 0.2%, 0.3%, 0.4%, 0.5%, 0.6%, 0.7%, 0.8%, 0.9%, 1%, 1.2%, 1.5%; Fe 0.01%, 0.02%, 0.05%, 0.1%, 0.2%, 0.3%, 0.4%, 0.5%, 0.6%, 0.7%, 0.8%, 0.9%, 0.1%; La 0.01%, 0.02%, 0.05%, 0.08%, 0.1%, 0.12%, 0.14%, 0.16%, 0.18%, 0.2%; Ce 0.01%, 0.02%, 0.05%, 0.08%, 0.1%, 0.12%, 0.14%, 0.16%, 0.18%, 0.2%, 0.22%, 0.24%, 0.26%, 0.28%, 0.3% and Yb 0.01%, 0.02%, 0.05%, 0.08%, 0.1%, 0.12%, 0.14%, 0.16%, 0.18%, 0.2%.

[0031] The present invention also incorporates three trace elements: Co, Ni, and Fe. The addition of these high-melting-point elements increases the melting point of the babbitt alloy, thereby raising the alloy's mechanical recrystallization temperature and effectively preventing the babbitt alloy layer from burning during semi-dry friction service. Furthermore, the Co and Ni react with Sn in the alloy matrix to form Co2Sn and Ni3Sn4 compounds, suppressing the formation of brittle FeSn and FeSn2 phases at the interface, thereby improving interfacial strength.

[0032] The present invention also incorporates three rare earth elements, La, Ce, and Yb. These three specific rare earth elements refine the alloy matrix, enhancing its plasticity, toughness, tensile strength, surface activity, and oxidation resistance. This reduces wire breakage due to oxidation inclusions during the drawing process, improves yield, and significantly enhances production efficiency. Furthermore, the rare earth elements enhance the solution's oxidation resistance, resulting in a bright, silvery-white metallic luster on the surface of the ingot and eliminating surface oxidation. The resulting babbitt alloy ingot can be directly extruded without the need for a peeling step, shortening the process and improving processing efficiency.

[0033] Furthermore, the three rare earth elements exhibit at least the following four technical benefits: First, the rare earth elements La and Ce have a strong tendency to interact with Sn, and both tend to form intermetallic compounds with Sn in the alloy system, i.e., they have a significant "Sn affinity" phenomenon, which leads to a decrease in Sn activity in the matrix. Therefore, theoretically, appropriate amounts of the rare earth elements La and Ce can inhibit the formation and growth of compounds in the matrix and at the interface, reducing the driving force for the formation of intermetallic compounds and improving interface reliability. Second, as active elements, the rare earth elements La and Ce tend to be enriched at the solution interface, thereby reducing the interfacial free energy, reducing the surface tension of the molten solder, and improving the flow properties of the tin-based alloy. Third, Yb is the second-to-last element in the lanthanide series of rare earth elements. Appropriate amounts of Yb can significantly improve the wettability, mechanical properties of the solder joint, thermal fatigue resistance, and creep resistance of the tin-based alloy. Fourthly, La and Ce are the first and second elements in the lanthanide series of rare earth elements. They have similar properties and are infinitely soluble. In addition, their total reserves in China account for 56%, which can reduce the raw material cost of the present invention to a certain extent compared with other rare earth elements.

[0034] The preparation method of the tin-based babbitt alloy comprises the following steps: S1, configuring the raw material components according to a weight ratio; the raw material components include Sn, Sb, Cu, Ni, Co, Fe, Cu80La8Ce12 and Sn60Yb40; S2, placing all the raw material components except Sn and part of the tin in a container for smelting to obtain a first molten liquid; after the smelting is completed, adding the remaining tin to the first molten liquid, carrying out a heat-insulating reaction, and obtaining a second molten liquid; S3, adding a refining agent to the second molten liquid, mixing it thoroughly, and then allowing it to stand for a treatment; after casting and molding, the tin-based babbitt alloy is obtained.

[0035] As a preferred embodiment, in step S1, the purity of each of the raw material components is ≥99.99%, that is, Sn, Sb, Cu, Ni, Co, Fe, Cu80La8Ce12 and Sn60Yb40 with a purity of 99.99% can be used.

[0036] As a preferred embodiment, in step S1, rare earth elements are added in the form of intermediate alloys Cu80La8Ce12 and Sn60Yb40 to effectively avoid element burnout and segregation; wherein Cu80La8Ce12 refers to an alloy containing 80% Cu, 8% La and 12% Ce by mass; Sn60Yb40 refers to an alloy containing 60% Sn and 40% Yb by mass.

[0037] It should be noted that when preparing the raw materials in step S1, the mass of Cu should be calculated comprehensively as the copper in pure copper and copper-lanthanum-cerium alloy, and the mass of Sn should be calculated comprehensively as the tin in pure tin and tin-ytterbium alloy.

[0038] As a preferred embodiment, in step S1, the raw material components can be in the form of any single substance or intermediate alloy, such as metal particles, metal blocks, metal ingots, metal powders, metal wires, metal sheets, etc., and the present invention is not limited to this.

[0039] As a preferred embodiment, in step S2, the partial tin is 40% to 60% of the mass of the Sn; as a more preferred embodiment, all raw material components except the Sn and 50wt% of the Sn are placed in a container for smelting to obtain a first molten liquid.

[0040] As a preferred embodiment, in step S2, the smelting is carried out under air-tight conditions to avoid oxidation and burning of the molten metal during the smelting process; the air-tight conditions can be carried out by one of the following methods (a) and (b), or by using both methods (a) and (b);

[0041] Method (a): providing a surface covering agent on the surface of the raw material component, wherein the surface covering agent comprises charcoal and / or dehydrated borax; as an optional embodiment, the covering thickness of the charcoal is 5 mm to 10 mm, and the thickness of the dehydrated borax is 1 mm to 3 mm.

[0042] Method (b), the smelting is carried out in a closed environment, and the smelting is an inert gas atmosphere; as an optional embodiment, the smelting container uses a graphite crucible or a silicon carbide crucible, and the inert gas uses nitrogen, helium, neon or argon.

[0043] As a preferred embodiment, in step S2, the smelting is induction smelting; the smelting temperature includes but is not limited to 800, 810, 820, 830, 840, 850, 860, 870, 880, 890, 900 (°C), and the smelting holding time includes but is not limited to 20, 25, 30, 35, 40 (min).

[0044] As a preferred embodiment, in step S2, the temperature of the insulation reaction includes but is not limited to 600, 610, 620, 630, 640, 650 (°C), and the time of the insulation reaction includes but is not limited to 20, 25, 30, 35, 40 (min).

[0045] Through heat preservation reaction, the nine elements of tin, antimony, copper, nickel, cobalt, iron, lanthanum, cerium and ytterbium react and diffuse with each other, producing a coupling effect, thereby improving the alloy structure, increasing the activity of the melt and enhancing the antioxidant performance, so as to achieve the purpose of strengthening the alloy performance and improving the machinability of the wire, thereby improving the processing efficiency and increasing the yield rate.

[0046] As a preferred embodiment, in step S3, the refining agent includes at least one of zinc chloride, ammonium chloride or sodium chloride; as a more preferred embodiment, the amount of the refining agent used is 0.05% to 0.1% of the mass of the tin-based babbitt alloy. The function of the refining agent is to reduce the content of oxygen, sulfur and non-metallic inclusions in the solution and improve the cleanliness of the solution.

[0047] As a preferred embodiment, in step S3, the standing treatment time includes but is not limited to 5, 6, 7, 8, 9, 10 (min), and the temperature of the melt after the standing treatment is 450°C to 500°C.

[0048] As a preferred embodiment, in step S3, the thorough mixing is performed by stirring, and the stirring rod can optionally be a high borosilicate glass rod or a high-purity graphite rod to achieve uniform composition of the melt; the stirring time is 3, 4, 5, 6, 7, 8 (min), and the stirring frequency is 120 rpm to 180 rpm.

[0049] Example 1

[0050] This embodiment provides a tin-based babbitt alloy, including the following elemental components in weight percentage: Sb 11%, Cu 6.5%, Ni 0.05%, Co 0.05%, Fe 0.01%, La 0.01%, Ce 0.015%, Yb 0.01%, and Sn balance.

[0051] The tin-based babbitt alloy provided in this embodiment is prepared by the following method steps:

[0052] (1) The raw materials are selected from the following components with a purity of 99.99%: tin ingot, pure copper particles, antimony block, iron powder, nickel wire, electrolytic cobalt sheet, Cu80La8Ce12, Sn60Yb40, and the raw materials are prepared according to the above weight percentages.

[0053] (2) After the configuration is completed, half of the tin and other raw materials are placed in a crucible, charcoal and dehydrated borax are used as surface covering agents to isolate the air, and the crucible is sealed and inert gas argon is introduced to reduce oxidation and burning of the solution during the smelting process.

[0054] (3) The raw materials were melted by induction melting process, with the initial melting temperature of 850 °C and the holding time of 30 minutes. After the raw material components were completely melted, the remaining tin ingots were added, and the solution temperature was adjusted to between 600 °C and kept warm for 40 minutes.

[0055] (4) After the insulation is completed, 0.1% of the total mass of the alloy is added to zinc chloride to refine the solution.

[0056] (5) The solution was stirred with a stirring rod for 5 minutes to homogenize the composition. The solution was then allowed to stand for 8 minutes, the melt temperature was controlled to between 450-500°C, the molten liquid was poured into a mold, and air-cooled to room temperature to obtain a tin-based babbitt alloy ingot.

[0057] (6) The ingot rod is heated, extruded, drawn, annealed, and drawn into a Babbitt alloy finished wire of 1.0 mm to 6.0 mm in multiple passes using an extruder and a wire drawing machine.

[0058] Figure 1 The metallographic microstructure of the Babbitt alloy wire obtained in this example under a 200 μm electron microscope is provided.

[0059] Example 2

[0060] This embodiment provides a tin-based babbitt alloy, including the following elemental components in weight percentage: Sb 11%, Cu 5.5%, Ni 0.9%, Co 0.8%, Fe 0.05%, La 0.1%, Ce 0.15%, Yb 0.08%, and Sn balance.

[0061] The preparation method of the tin-based babbitt alloy provided in this embodiment is exactly the same as that in Example 1.

[0062] Figure 2 The metallographic microstructure of the Babbitt alloy wire obtained in this example under a 200 μm electron microscope is provided.

[0063] Example 3

[0064] This embodiment provides a tin-based babbitt alloy, including the following elemental components in weight percentage: Sb 10%, Cu 6.5%, Ni 0.5%, Co 1.2%, Fe 0.08%, La 0.12%, Ce 0.18%, Yb 0.12%, and Sn balance.

[0065] The preparation method of the tin-based babbitt alloy provided in this embodiment is exactly the same as that in Example 1.

[0066] Figure 3 The metallographic microstructure of the Babbitt alloy wire obtained in this example under a 200 μm electron microscope is provided.

[0067] Example 4

[0068] This embodiment provides a tin-based babbitt alloy, comprising the following elemental components by weight percentage: Sb 10%, Cu 5.5%, Ni 1%, Co 1.5%, Fe 0.1%, La 0.2%, Ce 0.3%, Yb 0.2%, and the balance Sn.

[0069] The preparation method of the tin-based babbitt alloy provided in this embodiment is exactly the same as that in Example 1.

[0070] Figure 4 The metallographic microstructure of the Babbitt alloy wire obtained in this example under a 200 μm electron microscope is provided.

[0071] Example 5

[0072] This embodiment provides a tin-based babbitt alloy, the elemental composition of which is exactly the same as that of Example 1.

[0073] The preparation method of the tin-based babbitt alloy provided in this embodiment is substantially the same as that in Example 1, with the only difference being that the melting temperature in step (3) is 800°C and the holding time is 40 minutes; the solution temperature is then adjusted to 650°C and held for 20 minutes. In step (5), the solution is stirred with a stirring rod for 8 minutes and then allowed to stand for 5 minutes.

[0074] Example 6

[0075] This embodiment provides a tin-based babbitt alloy, the elemental composition of which is exactly the same as that of Example 1.

[0076] The preparation method of the tin-based babbitt alloy provided in this embodiment is substantially the same as that in Example 1, except that the melting temperature in step (3) is 900° C. and the holding time is 20 minutes. In step (5), the solution is stirred with a stirring rod for 3 minutes and then allowed to stand for 10 minutes.

[0077] Example 7

[0078] This embodiment provides a tin-based babbitt alloy, comprising the following elemental components by weight percentage: Sb 13%, Cu 8%, Ni 1%, Co 1.5%, Fe 0.1%, La 0.2%, Ce 0.3%, Yb 0.2%, and the balance Sn.

[0079] The preparation method of the tin-based babbitt alloy provided in this embodiment is exactly the same as that in Example 1.

[0080] Example 8

[0081] This embodiment provides a tin-based babbitt alloy, including the following elemental components by weight percentage: Sb 6%, Cu 3%, Ni 0.05%, Co 0.05%, Fe 0.01%, La 0.01%, Ce 0.01%, Yb 0.01%, and Sn balance.

[0082] The preparation method of the tin-based babbitt alloy provided in this embodiment is exactly the same as that in Example 1.

[0083] Comparative Example

[0084] A commercially available babbitt alloy with a brand number of 11-6 was used as a comparative example; it was passed through the same die as in Example 1, and subjected to multiple heating, extrusion, drawing, annealing, and drawing by an extruder and a wire drawing machine to a babbitt alloy wire of 1.0 mm to 6.0 mm for later use. Figure 5 The metallographic microstructure of the Babbitt alloy wire obtained in this comparative example under a 200 μm electron microscope is provided.

[0085] Test Example 1

[0086] The tin-based babbitt alloy wires obtained from each example and comparative example were tested for wire breakage rate. As shown in Table 1 below, the wires from each example experienced significantly fewer wire breaks under a unit pressure of 50 kg compared to the comparative example. This reduces the frequency of wire splicing for operators, improves wire drawing efficiency, and prevents wire breakage during field use due to splicing.

[0087] Table 1

[0088]

[0089]

[0090] Test Example 2

[0091] The surface quality of the tin-based babbitt alloy ingot obtained after step (5) is analyzed: Figure 6 It can be seen that the surface color of the alloy ingot of the comparative example is light yellow, and there is slight oxidation, while the surface of the ingot of Example 1 is bright, silvery white, and there is no oxidation, and the anti-oxidation performance is significantly improved.

[0092] Test Example 3

[0093] The side pore analysis of the tin-based babbitt alloy ingot obtained after step (5) is carried out: the side of the ingot is turned by a lathe to observe the distribution of subcutaneous pores on the side of the ingot. Figure 7 It can be seen that the side of the comparative ingot has dense small pores, while the surface of the ingot in Example 1 is bright, the number of pores is significantly reduced, and only small pores exist in a few local areas. This is beneficial to reduce the risk of alloy wire breaking at pores during the extrusion and drawing process.

[0094] Test Example 4

[0095] The babbitt alloy wires and steel substrates prepared in Example 2 and the comparative example were used to prepare babbitt alloy layers by additive manufacturing. The prepared workpieces were machined into standard bonding specimens on steel specimens. The bonding strength was tested using a universal mechanical testing machine. It can be seen that the bonding strength of Example 2 is higher than that of the comparative example. The specific experimental values ​​of the interface bonding strength are recorded in Table 2 below.

[0096] Table 2

[0097]

[0098]

[0099] Test Example 5

[0100] The elongation and tensile strength of each embodiment and comparative example were tested using a universal mechanical testing machine. It was found that the elongation at break and the tensile strength of the sample of each embodiment were significantly improved compared with the comparative example, indicating that the plastic toughness and tensile properties of the alloy were significantly improved, which further illustrates that the drawing properties of the wire were improved. The specific experimental values ​​of elongation at break and tensile strength are respectively recorded in Tables 3 and 4 below.

[0101] Table 3

[0102]

[0103]

[0104] Table 4

[0105]

[0106]

[0107] Although the present invention has been illustrated and described using specific embodiments, it should be appreciated that the above embodiments are merely intended to illustrate the technical solutions of the present invention rather than to limit them. Those skilled in the art should understand that the technical solutions described in the above embodiments may be modified, or some or all of the technical features thereof may be replaced by equivalents, without departing from the spirit and scope of the present invention. However, these modifications or replacements do not deviate from the essence of the corresponding technical solutions within the scope of the technical solutions of the embodiments of the present invention. Therefore, this means that all such replacements and modifications within the scope of the present invention are included in the appended claims.

Claims

1. A tin-based babbitt alloy, characterized in that: The tin-based babbitt alloy consists of the following elemental components by weight percentage: Sn 75%-90.86%, Sb 5.5%-14%, Cu 2.5%-9%, Ni 0.05%-1.5%, Co 0.05%-2%, Fe 0.01%-0.2%, La 0.01%-0.4%, Ce 0.01%-0.5% and Yb 0.01%-0.4%.

2. The tin-based babbitt alloy according to claim 1, characterized in that: The tin-based babbitt alloy consists of the following elemental components by weight percentage: Sn 75.7%-90.86%, Sb 6%-13%, Cu 3%-8%, Ni 0.05%-1%, Co 0.05%-1.5%, Fe 0.01%-0.1%, La 0.01%-0.2%, Ce 0.01%-0.3% and Yb 0.01%-0.2%.

3. The method for preparing the tin-based babbitt alloy according to claim 1 or 2, wherein: The preparation method comprises the following steps: S1. Prepare the raw material components according to weight ratio; the raw material components include Sn, Sb, Cu, Ni, Co, Fe, Cu80La8Ce12 and Sn60Yb40; S2, placing all raw material components except Sn and part of tin in a container for smelting to obtain a first molten liquid; After the smelting is completed, the remaining tin is added to the first molten liquid, and the mixture is kept warm for reaction to obtain a second molten liquid; S3, adding a refining agent to the second molten liquid, mixing thoroughly and then allowing to stand; and obtaining a tin-based babbitt alloy after casting.

4. The method for preparing the tin-based babbitt alloy according to claim 3, wherein: In step S2, the portion of tin is 40% to 60% of the mass of Sn.

5. The method for preparing the tin-based babbitt alloy according to claim 3, wherein: In step S2, the smelting is performed in an air-tight condition.

6. The method for preparing the tin-based babbitt alloy according to claim 5, characterized in that: A surface covering agent is arranged on the surface of the raw material component, wherein the surface covering agent comprises charcoal and / or dehydrated borax.

7. The method for preparing the tin-based babbitt alloy according to claim 5, characterized in that: The smelting is performed in a closed environment, and the smelting is an inert gas atmosphere.

8. The method for preparing tin-based babbitt alloy according to claim 3, characterized in that: In step S2, the smelting is induction smelting; The smelting temperature is 800° C. to 900° C., and the smelting holding time is 20 min to 40 min.

9. The method for preparing tin-based babbitt alloy according to claim 3, characterized in that: In step S2, the temperature of the heat preservation reaction is 600° C. to 650° C., and the time of the heat preservation reaction is 20 min to 40 min.

10. The method for preparing tin-based babbitt alloy according to claim 3, characterized in that: In step S3, the refining agent includes at least one of zinc chloride, ammonium chloride or sodium chloride; The amount of the refining agent used is 0.05% to 0.1% of the mass of the tin-based babbitt alloy.

11. The method for preparing tin-based babbitt alloy according to claim 3, characterized in that: In step S3, the standing treatment time is 5 minutes to 10 minutes, and the temperature of the melt after the standing treatment is 450° C. to 500° C.; And / or, in step S3, the thorough mixing is performed by stirring, and the stirring time is 3 minutes to 8 minutes.

12. Use of the tin-based babbitt alloy according to claim 1 or 2 in the preparation of a bearing bush, wherein the bearing bush is prepared by additive manufacturing technology.

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