CN115747566A - Performance improved Babbitt alloy formula and preparation process thereof - Google Patents
Performance improved Babbitt alloy formula and preparation process thereof Download PDFInfo
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- CN115747566A CN115747566A CN202211451603.4A CN202211451603A CN115747566A CN 115747566 A CN115747566 A CN 115747566A CN 202211451603 A CN202211451603 A CN 202211451603A CN 115747566 A CN115747566 A CN 115747566A
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Abstract
The invention discloses a property-improved babbitt metal formula which comprises the following components: the tin-based babbit alloy comprises, by mass, 10.0-12.0% of Sb, 5.5-6.5% of Cu, 0.35% of Pb and 0.03-1% of Nd, and is characterized in that Ag and Nd are added into a tin-based babbit alloy B83 to generate a new point-like hard phase which is uniformly distributed in a crystal boundary of the alloy, so that the density of the hard phase in a metallographic phase is increased, the high-temperature hardness of the alloy is improved, the compressive strength of the alloy after the Ag and the Nd are added is increased to different degrees, after the Ag and the Nd are added, the beta phase and the epsilon phase of the B83 are fine and uniformly distributed, the heat is uniformly distributed during friction, and meanwhile, a part of friction generated hard phase fills up a pit generated during friction, the wear resistance is improved, the hardness, the compressive strength and the wear resistance of the improved tin-based babbit alloy are improved, and the research and development of high-end sliding bearings are promoted.
Description
Technical Field
The invention relates to the technical field of babbitt metal preparation processes, in particular to a property-improved babbitt metal formula and a preparation process thereof.
Background
The tin-based babbit alloy has lower expansion coefficient and friction factor, and good wear resistance, corrosion resistance, heat conductivity and toughness, is widely applied to the surfaces of sliding bearings of mechanical devices such as steam turbines, internal combustion engines, nuclear power units and the like, plays roles in shock absorption, wear resistance and abrasion resistance, is vital to improving the operation efficiency of the mechanical devices, and the rotary machinery is developing towards the direction of high speed, heavy load and high precision at present, and has higher and higher requirements on the sliding bearings;
however, the performance of the existing tin-based babbitt alloy does not meet the requirement of high precision development of rotating machinery, and the performances of high bearing capacity and high wear resistance are still to be improved.
Disclosure of Invention
The invention provides a property-improved Babbitt alloy formula and a preparation process thereof, which can effectively solve the problems that the performance of the existing tin-based Babbitt alloy in the background art does not meet the requirement of high precision development of a rotary machine, and the performance of high bearing and high wear resistance is still to be improved.
In order to achieve the purpose, the invention provides the following technical scheme: a property-improved Babbitt alloy formula comprises the following components: sn, sb, cu, pb, nd, ag;
the mass fraction of Sb is 10.0-12.0%;
the mass fraction of Cu is 5.5-6.5%;
the mass fraction of Pb is 0.35 percent;
the mass fraction of Nd is 0.03-1%;
the mass fraction of Ag is 0.1-1%.
According to the technical scheme, the method comprises the following steps:
s1, preparing and cleaning materials;
s2, melting the tin-based Babbitt alloy, and adding a stirring device;
s3, adding new alloy components;
s4, emulsifying and shearing at a high speed;
and S5, heat preservation treatment.
According to the technical scheme, in the S1, the required materials comprise basic tin-based Babbitt B83, ag powder and rare earth element Nd powder;
the basic tin-based babbit alloy B83 is in a block shape, and the main components of the basic tin-based babbit alloy B83 are Sn, sb and Cu; ag. And Nd is granular with the granularity of 200 meshes, ag powder is weighed according to the proportion of 0.1-1%, nd powder is weighed according to the proportion of 300PPM-0.1%, the Nd powder is cleaned for 10min by an ultrasonic cleaner, and then the Nd powder is packaged in vacuum for standby.
According to the technical scheme, in the step S2, the tin-based Babbitt B83 is placed in a resistance furnace to be heated and melted, after the temperature is raised to 480 ℃, the temperature is kept for 20 minutes, oxide floating slag on the surface of the molten alloy is scraped, a stirring device is added, and a stirring blade is immersed into the alloy liquid level for 5-10CM;
the stirring device controls the rotating speed to 2000 r/min, stirs for 60 min, and carries out alloy melting treatment on the tin-based babbit alloy B83.
According to the technical scheme, in the step S3, the weighed Ag and rare earth element Nd powder is added into the molten tin-based babbitt metal B83;
and starting the stirring device to fully melt the alloy and the powder.
According to the technical scheme, in the step S4, the rotating speed is controlled to be about 2000 r/min and 60 min, and new components are completely dispersed in the alloy.
According to the technical scheme, in the step S5, after the alloy is fully melted, the temperature of the resistance furnace is controlled at 300 ℃, the temperature is kept for 1 hour, and the metallographic structure of the alloy is solidified.
According to the technical scheme, in S5, after heat preservation treatment, a performance test is carried out on the prepared performance-improved babbitt alloy.
According to the technical scheme, the performance test comprises a mechanical performance test and a tribology performance test;
testing the Brinell hardness and the compressive strength of the alloy by a mechanical property test;
the tribology performance test tests the coefficient of friction and the amount of wear.
Compared with the prior art, the invention has the following beneficial effects:
by adding Ag and Nd into the tin-based babbit alloy B83, a new punctiform hard phase is generated and is uniformly distributed in the crystal boundary of the alloy, so that the density of the hard phase in a metallographic phase is increased, the high-temperature hardness of the tin-based babbit alloy is further improved, the compressive strength after the Ag and the Nd are added is increased in different degrees, the beta-phase and epsilon-phase tissues of the B83 are fine and uniformly distributed after the Ag and the Nd are added, the heat is uniformly distributed during friction, meanwhile, a part of friction generated pits are filled with the newly generated hard phase, the wear resistance is improved, the hardness, the compressive strength and the wear resistance of the improved tin-based babbit alloy are improved, and the research and development of high-end sliding bearing products are promoted;
in the preparation process, a mixed powder hot pressing process is adopted, materials are added and stirred under the condition of a tin-based babbit alloy liquid phase, so that the added materials and the original tin-based babbit alloy are uniformly distributed, the novel babbit alloy composite material containing different component proportions is prepared, and the occurrence of segregation phenomenon in a high-temperature state is avoided.
Drawings
The accompanying drawings, which are included to provide a further understanding of the invention and are incorporated in and constitute a part of this specification, illustrate embodiments of the invention and together with the description serve to explain the principles of the invention and not to limit the invention.
In the drawings:
FIG. 1 is a schematic structural view of the present invention;
FIG. 2 is a diagram of a process line and associated apparatus of the present invention;
FIG. 3 is a schematic view of the structure of the Brinell hardness measuring device of the present invention;
FIG. 4 is a graphical representation of hardness versus temperature before and after B83 modification according to the present invention;
FIG. 5 is a gold phase diagram of a sample after a frictional wear test of the present invention.
Detailed Description
The preferred embodiments of the present invention will be described in conjunction with the accompanying drawings, and it will be understood that they are described herein for the purpose of illustration and explanation and not limitation.
Example (b): as shown in figure 1, the invention provides a technical scheme, and a property-improved babbitt metal formula comprises the following components: sn, sb, cu, pb, nd, ag;
the mass fraction of Sb is 11%;
the mass fraction of Cu is 6%;
the mass fraction of Pb is 0.35 percent;
the mass fraction of Nd is 0.5%;
the mass fraction of Ag is 0.5%;
the mass fraction of Sn is 81.65%.
As shown in fig. 2, according to the above technical solution, the method comprises the following steps:
s1, preparing and cleaning materials;
s2, melting the tin-based babbitt metal, and adding a stirring device;
s3, adding new alloy components;
s4, emulsifying and shearing at a high speed;
and S5, heat preservation treatment.
According to the technical scheme, in S1, the required materials comprise basic tin-based Babbitt B83, ag powder and rare earth element Nd powder;
the basic tin-based babbit alloy B83 is in a block shape, and the main components of the basic tin-based babbit alloy B83 are Sn, sb and Cu; ag. And Nd is granular with the granularity of 200 meshes, ag powder is weighed according to 0.5 percent, nd powder is weighed according to 0.1 percent, the Ag powder and the Nd powder are cleaned for 10min by an ultrasonic cleaner, and then the Ag powder and the Nd powder are vacuum-packaged for later use.
According to the technical scheme, in the step S2, the tin-based Babbitt alloy B83 is placed in a resistance furnace to be heated and melted, after the temperature is raised to 480 ℃, the temperature is kept for 20 minutes, oxide floating slag on the surface of the molten alloy is scraped, a stirring device is added, and stirring blades are immersed into the alloy liquid level by 8CM;
the stirring device controls the rotating speed to 2000 r/min, stirs for 60 min, carries on the alloy melting process to the tin-based babbitt alloy B83.
According to the technical scheme, in S3, the weighed Ag and rare earth element Nd powder is added into the molten tin-based babbitt metal B83;
and starting the stirring device to fully melt the alloy and the powder.
According to the technical scheme, in S4, the rotating speed is controlled to be about 2000 rpm and 60 minutes, and the new components are completely dispersed in the alloy.
According to the technical scheme, in S5, after the alloy is fully melted, the temperature of the resistance furnace is controlled at 300 ℃, the temperature is kept for 1 hour, and the metallographic structure of the alloy is solidified.
According to the technical scheme, in S5, after the heat preservation treatment, the performance test is carried out on the prepared performance-improved babbitt metal.
According to the technical scheme, the performance test comprises a mechanical performance test and a tribology performance test;
testing the Brinell hardness and the compressive strength of the alloy by a mechanical property test;
the tribology performance test tests the coefficient of friction and the amount of wear.
As shown in FIG. 3, the Brinell hardness tester is HB-3000, the test standard is GB231.1-2002 Metal Brinell hardness test, the diameter of a steel ball in the test is 5mm, the load P is 250kgf, the load holding time is 30s, the measurement temperature range is 30-120 ℃, hardness sampling is carried out at intervals of 10 ℃, the average value is taken as the Brinell hardness at the temperature, the crystallization distribution quality in the metallographic structure of the Babbitt B83 before and after improvement is quantitatively evaluated, and the following quantitative evaluation table is prepared:
as shown in fig. 4, from the babbitt hardness test before and after the improvement, the brinell hardness values of B83 after adding Ag and Nd were improved in the range of 30 to 120 ℃, because the addition of Ag and Nd affected the size and distribution of the β phase, the β phase size decreased by 41.6%, the β phase size decreased by 45.8% after adding 1%, and the hardness value after adding 1%was slightly higher than that after adding rare earth element Nd, and the brinell hardness value after adding 1 ÷ Ag increased by 8.6% on average at 105 ℃ (bearing alarm temperature), because the addition of Ag and Nd generated a new dot-like hard phase ((Cu, nd + Ag) Sn 2) and was uniformly distributed in the grain boundary of the alloy, so that the hard phase density in the metallographic phase was increased from 42.1% to 46.5%, the B83 structure was more uniform, and the high temperature hardness was further improved.
Compressive strength is also an important indicator for evaluating the performance properties of Babbitt alloys, where compressive strength is measured on an Instron5500R electronic tensile compression tester, according to the Standard GB/T7314-2005 metallic Material Room temperature compression test method, where the distance between the upper and lower clamps is 26mm and the test loading rate is 1mm/min.
From the test results of the compressive strength, it can be seen that the compressive strength of B83 is slightly increased by 1.4% and 1.9% after adding Ag (0.1% and 1%), and the compressive strength of B83 is increased by 8.1% after adding Nd (1%) compared with the original B83, because the addition of Nd does not form a new phase with other materials, so that the strength of B83 is enhanced, and the compressive strength values before and after the improvement of B83 are shown in the following table:
in the tribology performance test, the test equipment is a UMT-2 type multifunctional friction and wear tester, the tested parameters comprise a friction coefficient f and a wear loss delta m, the test adopts a pin-disc opposite grinding mode, the test is carried out under dry friction, the pin is made of Babbitt alloy to be tested, the size is phi 6mm multiplied by 15mm, the disc is made of 45# steel, the size is phi 30mm multiplied by 5mm, the roughness of the pin and the disc surface is Ra0.8, the friction coefficient test time is 10min, the wear loss test time is 30min, the wear loss is obtained through the mass loss of the pin before and after the test, the measurement equipment is an electronic balance with the precision of 0.1mg, the test parameters refer to the use working conditions of a high-speed machine tool and a micro gas turbine, the pv value (wherein p is a unit area load, v is a linear velocity) of the test is 20 MPa.m.s < - > -1, and the friction and wear test parameters are set during the test as shown in the following table:
as shown in fig. 5, it can be seen from the metallographic images of the samples after the frictional wear test that a large number of pits are present on the wear surface due to the molten wear of the babbit wear surface, and a large amount of heat generated during the frictional wear is hard to disappear by conduction and radiation, and the frictional heat accumulation increases the surface temperature, and when the temperature approaches the melting point of α solid solution, the surface energy is made to flow by the frictional force, so that a part of the hard particles is separated from the friction surface, and a part of the hard particles is broken into small particles to remain on the system surface, wherein the number of pits is the largest in (a) in fig. 5, which is because the hard particles in the original B83 are coarse in structure and are unevenly distributed, and heat is concentrated, resulting in severe wear, and the pits are small in (B), (c), and (d) in fig. 5, and because the structures of the β phase and the e phase of B83 are fine and evenly distributed after Ag and Nd are added, so that the heat is evenly distributed, and at the same time, the newly generated hard phase ((Cu, nd + Ag) Sn 2) fills a part of the pits in fig. 5, so are the number of pits is the smallest, and the average friction coefficient of the wear before and the amount before and after the improvement are as shown as follows:
finally, it should be noted that: although the present invention has been described in detail with reference to the foregoing embodiments, it will be apparent to those skilled in the art that modifications may be made to the embodiments described above, or equivalents may be substituted for elements thereof. Any modification, equivalent replacement, or improvement made within the spirit and principle of the present invention should be included in the protection scope of the present invention.
Claims (9)
1. A property-improved Babbitt alloy formula is characterized in that: comprises the following components: sn, sb, cu, pb, nd, ag;
the mass fraction of Sb is 10.0-12.0%;
the mass fraction of Cu is 5.5-6.5%;
the mass fraction of Pb is 0.35 percent;
the mass fraction of Nd is 0.03-1%;
the mass fraction of Ag is 0.1-1%.
2. The process for preparing babbitt metal with improved properties according to claim 1, comprising the steps of:
s1, preparing and cleaning materials;
s2, melting the tin-based babbitt metal, and adding a stirring device;
s3, adding new alloy components;
s4, emulsifying and shearing at a high speed;
and S5, heat preservation treatment.
3. The improved babbitt metal preparation process of claim 2, wherein in S1, the required materials comprise basic tin-based babbitt metal B83, ag powder and rare earth element Nd powder;
the basic tin-based Babbitt B83 is blocky, and the main components of the basic tin-based Babbitt B83 are Sn, sb and Cu; ag. And Nd is granular with the granularity of 200 meshes, ag powder is weighed according to the proportion of 0.1-1%, nd powder is weighed according to the proportion of 300PPM-0.1%, the Nd powder is cleaned for 10min by an ultrasonic cleaner, and then the Nd powder is packaged in vacuum for standby.
4. The process of claim 1, wherein in step S2, the tin-based babbitt metal B83 is melted by heating in an electric resistance furnace, and after the temperature is increased to 480 ℃, the temperature is maintained for 20 minutes, oxide scum on the surface of the melted metal is scraped off, a stirring device is added, and stirring blades are submerged in the metal surface for 5 to 10CM;
the stirring device controls the rotating speed to 2000 r/min, stirs for 60 min, and carries out alloy melting treatment on the tin-based babbit alloy B83.
5. The improved babbitt metal preparation process according to claim 1, wherein in S3, weighed Ag and rare earth element Nd powder is added into molten tin-based babbitt metal B83;
and starting the stirring device to fully melt the alloy and the powder.
6. The process of claim 1, wherein in step S4, the rotation speed is controlled to be about 2000 rpm and 60 minutes, and the new components are completely dispersed in the alloy.
7. The process of claim 1, wherein in the step S5, after the alloy is fully melted, the temperature of the resistance furnace is controlled at 300 ℃, the temperature is kept for 1 hour, and the metallographic structure of the alloy is solidified.
8. The process of claim 1, wherein in S5, after the heat preservation treatment, the performance of the prepared Babbitt metal is tested.
9. The process of claim 8, wherein the performance tests comprise mechanical performance tests and tribological performance tests;
testing the Brinell hardness and the compressive strength of the alloy by a mechanical property test;
the tribology performance test tests the coefficient of friction and the amount of wear.
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Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101935775A (en) * | 2009-06-29 | 2011-01-05 | 上海飞轮有色冶炼厂 | Rare-earth-containing bearing alloy and preparation method thereof |
| CN102220516A (en) * | 2011-06-24 | 2011-10-19 | 哈尔滨工业大学 | High-plasticity tin-based Babbitt alloy |
| CN102242293A (en) * | 2011-06-24 | 2011-11-16 | 哈尔滨工业大学 | Tin-based babbitt |
| CN104263995A (en) * | 2014-10-09 | 2015-01-07 | 戴国水 | Titanium-based alloy wire |
| CN107354329A (en) * | 2017-06-06 | 2017-11-17 | 西安交通大学 | ZChSnSb11 6 improves the method that tribological property refines with β phases |
| CN107365923A (en) * | 2017-07-18 | 2017-11-21 | 西安交通大学 | The method of the passivation of ZChSnSb11 6 β phase grain shape wedge angles |
| CN113416866A (en) * | 2021-06-29 | 2021-09-21 | 南京青锐风新材料科技有限公司 | Lead-free solder oxidation resistant alloy and production and preparation process thereof |
-
2022
- 2022-11-18 CN CN202211451603.4A patent/CN115747566A/en active Pending
Patent Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101935775A (en) * | 2009-06-29 | 2011-01-05 | 上海飞轮有色冶炼厂 | Rare-earth-containing bearing alloy and preparation method thereof |
| CN102220516A (en) * | 2011-06-24 | 2011-10-19 | 哈尔滨工业大学 | High-plasticity tin-based Babbitt alloy |
| CN102242293A (en) * | 2011-06-24 | 2011-11-16 | 哈尔滨工业大学 | Tin-based babbitt |
| CN104263995A (en) * | 2014-10-09 | 2015-01-07 | 戴国水 | Titanium-based alloy wire |
| CN107354329A (en) * | 2017-06-06 | 2017-11-17 | 西安交通大学 | ZChSnSb11 6 improves the method that tribological property refines with β phases |
| CN107365923A (en) * | 2017-07-18 | 2017-11-21 | 西安交通大学 | The method of the passivation of ZChSnSb11 6 β phase grain shape wedge angles |
| CN113416866A (en) * | 2021-06-29 | 2021-09-21 | 南京青锐风新材料科技有限公司 | Lead-free solder oxidation resistant alloy and production and preparation process thereof |
Non-Patent Citations (1)
| Title |
|---|
| 王建梅著: "《油膜轴承结合强度理论》", vol. 1, 冶金工业出版社, pages: 5 - 6 * |
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