CN112458332A - Titanium bronze alloy bar and preparation method and application thereof - Google Patents
Titanium bronze alloy bar and preparation method and application thereof Download PDFInfo
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C9/00—Alloys based on copper
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
- B21C23/00—Extruding metal; Impact extrusion
- B21C23/02—Making uncoated products
- B21C23/04—Making uncoated products by direct extrusion
- B21C23/08—Making wire, bars, tubes
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
- B21C31/00—Control devices, e.g. for regulating the pressing speed or temperature of metal; Measuring devices, e.g. for temperature of metal, combined with or specially adapted for use in connection with extrusion presses
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
- B21C37/00—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape
- B21C37/04—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape of bars or wire
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/0075—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for rods of limited length
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/08—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of copper or alloys based thereon
Abstract
The invention discloses a titanium bronze alloy bar which comprises the following components in percentage by mass: 1.5-2.5% of Ti, 0.01-0.5% of Mg, 0.01-1.0% of element X, and the balance of copper and inevitable impurities, wherein X is at least one element of Cr, Fe, Co and Ni. The alloy bar has excellent strength and high-temperature softening resistance, improved conductivity, tensile strength of more than 1000MPa, conductivity of more than 15% IACS, softening temperature of more than 500 ℃, good comprehensive performance, and capability of meeting the requirements of industries such as electronics, electricians, connectors, welding, heavy-duty machinery, hydraulic pressure and the like; the titanium bronze alloy can be processed into bars, has good casting property and processing property, is suitable for large-scale industrialization, and provides good application prospect for the application of the titanium bronze alloy bars in the industries of electronics and electricians, connectors, welding, heavy-duty machinery, hydraulic pressure and the like.
Description
Technical Field
The invention relates to the technical field of copper alloy, in particular to a titanium bronze alloy bar and a preparation method and application thereof.
Background
Tin bronze is commonly used for manufacturing elastic elements and wear-resistant parts due to good mechanical properties and wear resistance, and is widely applied to the electrical industry, light industry, mechanical manufacturing, building industry and even defense industry. However, the characteristics of tin bronze itself have the following problems: the tin bronze has a large range of solidification temperature, poor casting fluidity, easy segregation especially when the tin content is high, deterioration of casting performance and even possible generation of other defects, and low production yield; tin is an alloy element with higher market price, and from the aspect of economic benefit, the production cost is greatly improved due to high tin content and low yield. The development of tin bronze substitute materials has also received considerable attention.
Among them, titanium bronze alloys have received much attention due to their excellent strength, fatigue resistance and workability, and have been used in many fields. The American designation of titanium bronze alloy as representative is C19900. The titanium content in the C19900 alloy is more than 2.9 percent, and high strength can be realized through the thermomechanical treatment process, but the condition that solid solution titanium cannot be fully precipitated cannot be avoided due to excessively high titanium content, so that the conductivity of the titanium bronze is reduced. In addition, the tendency of oxidation slagging is more serious in the smelting process due to the overhigh Ti content, the component uniformity of the alloy is not easy to control, and the industrialization difficulty of the high-content titanium bronze is higher due to the combination of the above factors.
On the one hand, the existing titanium bronze alloy has no advantages in electrical conductivity compared with tin bronze with higher tin content, and cannot completely replace tin bronze in the environment requiring higher electrical conductivity. If the conductivity of the titanium bronze alloy can be further improved, the application requirement can be better met. On the other hand, from the viewpoint of industrial popularization, the titanium content is reduced, and the casting characteristics and the processing characteristics of the alloy can be improved to a certain extent. In view of the above purpose, the invention provides a titanium bronze alloy bar and a preparation method and application thereof.
Disclosure of Invention
The technical problem to be solved by the invention is to provide a titanium bronze alloy bar with excellent strength and high-temperature softening resistance and improved conductivity, and a preparation method and application thereof, aiming at the defects of the prior art, wherein the titanium bronze alloy bar has the advantages of tensile strength of more than 1000MPa, conductivity of more than 15% IACS, softening temperature of more than 500 ℃, good comprehensive performance, and capability of meeting the requirements of industries such as electronics, electricians, connectors, welding, heavy-load machinery, hydraulic pressure and the like.
The technical scheme adopted by the invention for solving the technical problems is as follows: a titanium bronze alloy bar comprises the following components in percentage by mass: 1.5-2.5% of Ti, 0.01-0.5% of Mg, 0.01-1.0% of element X, and the balance of copper and inevitable impurities, wherein X is at least one element of Cr, Fe, Co and Ni.
According to the invention, by introducing the alloy element Mg and the alloy element X into the titanium bronze alloy with medium and low titanium contents (1.5-2.5%), and forming an intermetallic compound with the titanium element which is not fully precipitated, the strength of the titanium bronze alloy is further improved, so that the strength of the titanium bronze alloy with medium and low titanium contents can reach the level of the titanium bronze alloy with high titanium content; and the conductivity of the titanium bronze alloy is further improved by reducing the content of solid solution titanium. In addition, compared with the existing titanium bronze alloy, the titanium bronze alloy also has better high-temperature softening resistance.
The Ti in the titanium bronze alloy is used as a main alloy element, the maximum solid solubility of the Ti in a copper matrix is 4.7% at 896 ℃, and the solid solubility is obviously reduced along with the reduction of the temperature. Titanium bronze alloys are a typical age-strengthening type of alloy that can be hardened by precipitation of the gamma phase of a Cu-Ti compound. The Ti element content has great influence on the mechanical properties of the alloy, particularly the conductivity, and the Ti also has the characteristic of grain refinement. When the Ti content is more than 2.5%, the conductivity of the alloy can be obviously reduced, and the casting difficulty of the alloy can be increased; when the Ti content is less than 1.5%, it is difficult to obtain a desired strength. In order to take account of the influence of Ti on the alloy strength, the electric conductivity and the casting characteristic, the content of Ti element in the titanium bronze alloy bar is controlled within the range of 1.5-2.5%, and the preferable range is 1.7-2.1%.
On one hand, Mg has the function of solid solution strengthening, and on the other hand, Mg is also a commonly used deoxidizer for copper alloy smelting. The proper amount of Mg is added into the titanium bronze alloy, so that the content of solid solution Ti in a matrix can be reduced to a certain extent, the precipitation of a Cu-Ti phase is promoted, and the conductivity of the titanium bronze is improved. In addition, Mg and Cu also form Cu with high hardness2The Mg phase and the Cu-Ti phase which is dispersed in the matrix jointly play a role in stopping dislocation movement, thereby further improving the mechanical property of the material. If the content of Mg is more than 0.5%, the conductivity of the alloy is reduced to a certain extent; if the Mg content is less than 0.01%, no significant strengthening effect is produced. Therefore, the range of the Mg content in the titanium bronze alloy bar is controlled to be 0.01-0.5%, and preferably 0.02-0.2%.
The maximum solid solubility of Cr in a copper matrix at 1076 ℃ is 0.65%, and the solid solubility is obviously reduced along with the reduction of the temperature, so that the CuCr alloy is a typical aging strengthening alloy. The influence of Cr on the conductivity of the copper alloy is far less than that of Ti, but the Cr content is too high, so that the obvious Cr phase aggregation and coarsening phenomenon can be generated, and the strengthening effect of the alloy is influenced. In addition, Cr has the functions of refining grains and improving the heat resistance of the alloy. A proper amount of Cr element is added into the titanium bronze alloy, so that the strength of the alloy can be further improved, and the conductive property of the alloy can be optimized. In order to take the influence of Cr on the strength and the conductivity of the titanium bronze alloy into consideration, the Cr content needs to be controlled, and if the Cr content is too high, the risk of stress cracking is increased due to the aggregation of Cr phases; if the Cr content is too low, no significant effect on the alloy can be obtained.
Fe can refine copper alloy crystal grains, improve the high-temperature strength of the copper alloy and promote the uniform distribution of an aging treatment precipitated phase. Fe and Ti can form Fe-Ti intermetallic compounds, promote the precipitation of Ti in the titanium bronze alloy and improve the conductivity of the alloy. Since Ti element having a large effect of decreasing the electric conductivity is added to the alloy, the amount of Fe element added should be limited in order to balance the strength and electric conductivity of the alloy. If the Fe content is too low, the strengthening effect of the Fe element cannot be achieved; if the Fe content is too high, the conductive performance of the alloy deteriorates.
Ni is infinitely solid-dissolved in Cu, and the matrix strength can be improved by solid-solution strengthening. In the invention, Ni has more important function of forming a Ni-Ti phase with Ti in the titanium bronze alloy, promoting the precipitation of Ti, and not reducing the conductivity of the alloy while improving the strength of the alloy. If the Ni content is too low, the improvement on the alloy strength is not obvious; when the Ni content is too high, the conductivity of the alloy is significantly reduced.
The effect of Co in the copper alloy is similar to that of Fe and Ni, and the Co can play a role in refining grains and improving the strength of the alloy. Co and Ti can also form a Co-Ti intermetallic compound, which plays a beneficial role in the precipitation of Ti in the titanium bronze alloy, thereby improving the conductivity of the alloy. If the Co content is too low, the effect of improving the alloy strength is not obvious; when the Co content is too high, the conductivity of the alloy is lowered.
The addition of Cr, Fe, Co and Ni elements can improve the mechanical property of the titanium bronze alloy bar. The proper amount of Cr, Fe, Co and Ni can improve the mechanical property of the alloy and simultaneously can not cause obvious negative effect on the conductivity of the alloy. Therefore, the invention selects and adds at least one element of Cr, Fe, Co and Ni, and the total content is controlled in the range of 0.01-1.0%.
Preferably, in the microstructure of the cross section of the titanium bronze alloy bar of the present invention, Cu is incorporated2The total area of the Mg phase is recorded as M, the sum of the total areas of the Fe-Ti phase, the Ni-Ti phase, the Co-Ti phase and the Cr phase is recorded as N, and the ratio of M to N is controlled to be 0.01-5. For the aging strengthening type titanium bronze alloy, the electric conductivity is mainly determined by soluteThe solid solution degree of Ti in the matrix is determined, and the higher the solid solution degree is, the larger the blocking effect of the material on electrons is, and the worse the finally obtained electric conductivity is. After the third alloy element Mg is introduced, the solid solution degree of Ti is reduced, and the aging precipitation is more sufficient. Cu2The Mg phase is the most main strengthening phase in the titanium bronze alloy, completely enters the matrix after solution treatment to form supersaturated solid solution, and uses Cu as the aging process2Mg is separated out, so that the matrix is purer, the barrier effect on electrons is reduced, and the conductivity of the alloy is improved. On the other hand due to Cu2The hardness of Mg phase is high, and dislocation lines bypass Cu in the plastic deformation process2The Mg phase forms dislocation loops. As the dislocation line continues to move, a dislocation plug product effect is formed in a hard phase region, so that the subsequent dislocation line is difficult to bypass, and the plastic deformation resistance, namely the strengthening effect of the alloy is increased continuously.
The formation of dispersed precipitated phases such as Fe-Ti phase, Ni-Ti phase, Co-Ti phase and Cr phase and the formation of Cu2Mg is similar. The formation of these dispersed precipitates reduces the amount of Ti solid solution in the copper matrix and promotes Cu on the one hand4Separating out Ti; on the other hand, Ti in solid solution is replaced to reduce the blocking effect on electrons, so that the conductivity of the alloy is improved. Wherein the Ni-Ti phase is used as a primary phase and can be used as Cu in the aging process of the alloy2The nucleation center of the Mg phase further improves the refinement degree and the distribution condition of the precipitated phase, and the mechanical property of the alloy is further improved in a more dispersed distribution form by refining the precipitated phase. However, the strengthening effect of these elements dispersed and precipitated on the alloy is not as good as the content is larger. When the amount of the additive is too large, an excessive amount of intermetallic compounds such as Fe-Ti phase, Ni-Ti phase, and Co-Ti phase are formed, resulting in Cu which is a main strengthening effect in the matrix4The Ti phase quantity is reduced, and the mechanical property of the alloy is reduced.
In one aspect of the invention, Cu is formed by Mg2The Mg phase reduces the solid solution degree of Ti element in the matrix, and on the other hand, the Fe, Ni, Co and other elements form intermetallic compounds with Ti to increase the precipitation ratio of solid solution Ti, thereby improving the conductivity of the titanium bronze alloy to the maximum extentAnd simultaneously reduces the influence of precipitation on other mechanical properties. Finally, through a great deal of tests, the invention discovers that Cu is mixed by the components and the process2The ratio of the total area of the Mg phase to the sum of the total areas of the Fe-Ti phase, the Ni-Ti phase, the Co-Ti phase and the Cr phase is controlled to be 0.01-5, so that the synergistic strengthening effect of the two precipitation strengthening phases can achieve the best effect.
Preferably, the microstructure of the cross section of the titanium bronze alloy bar according to the invention has an individual area of less than 0.01. mu.m2The number of precipitated phases of (2) is more than 1X 106Per mm2. Because the quantity, size and form of the second phase particles and the distribution mode of the second phase particles in the matrix can influence the integral strengthening effect, the invention can ensure that a more uniform and dispersed strengthening phase can be formed under the condition of influencing the mechanical property of the alloy as little as possible by controlling the quantity of precipitated phases with specific areas, thereby optimizing the integral strengthening effect of the alloy.
Preferably, the titanium bronze alloy bar of the invention further comprises at least one element of B, Ce and Zr in a total amount of 0.001-0.5% by mass. B. Ce and Zr in the alloy not only have the functions of deoxidizing and purifying melts, but also can obviously refine grains, and simultaneously can promote the uniform distribution of tissues, thereby being beneficial to the improvement of comprehensive properties. However, when the content of B, Ce or Zr exceeds 0.5%, the effect cannot be further exerted to a significant extent, and the workability of the alloy is deteriorated. Therefore, in the titanium bronze alloy bar, the total amount of at least one element of B, Ce and Zr is controlled to be 0.001-0.5%.
The titanium bronze alloy can be processed into bars according to different application requirements. The preparation method of the titanium bronze alloy bar comprises the following steps: fusion casting → extrusion → solid solution → stretching → primary aging → stretching → secondary aging, which is specifically as follows:
(1) casting: the titanium bronze alloy can be cast by adopting semi-continuous casting or full-continuous casting, the smelting temperature is controlled to be 1300-1350 ℃, the heat preservation time is controlled to be 15-30 min, and the burning loss of active elements is aggravated when the smelting temperature is too high or the heat preservation time is too long; if the melting temperature is too low or the holding time is too short, the high-melting-point metal elements are difficult to be sufficiently melted.
(2) Extruding: in order to ensure that the microstructure and the surface quality of an extruded product meet the control requirements, the extrusion temperature of the alloy is controlled to be 900-1000 ℃, the extruded blank needs to be rapidly cooled by at least 300 ℃/s immediately after extrusion so as to be rapidly cooled to be below 500 ℃, coarse precipitated phases are avoided, and then the extruded blank is cooled to be below 50 ℃ at a cooling speed of 100-300 ℃/s.
(3) Solid solution: as described above, the rapid cooling of the extruded material during extrusion can also provide a certain solid solution effect, but it is difficult to achieve a sufficient solid solution effect in this process. Therefore, in order to improve the performance of the alloy to the maximum extent, it is necessary to perform sufficient solid solution treatment on the extrusion billet to form a supersaturated solid solution, so as to provide thermodynamic potential for the later aging precipitation process. The supersaturation degree of the solute depends on the solid solution temperature to a great extent, so the selection of the solid solution temperature is very important, the solid solution temperature of the alloy is controlled to be 800-1000 ℃, preferably 900-980 ℃, the selection of the heat preservation time needs to be properly adjusted by combining the specification size of the material, and the heat preservation time is correspondingly prolonged when the specification is larger. The solid solution heat preservation time of the alloy is 1-60 min. After heat preservation, the material needs to be rapidly cooled, the cooling speed needs to reach more than 300 ℃/s, and the best solid solution effect can be achieved, because when the solute reaches the maximum solid solubility, rapid cooling can lead the solid solution into the copper matrix to be separated out in time of solute atoms, and when the temperature is cooled to room temperature, the solid solubility of the solute atoms in the alloy reaches the maximum. The precipitated phase Cu required by the invention can be obtained by matching with the subsequent cold deformation and aging process2The ratio of the total area of Mg to the sum of the total areas of the Fe-Ti phase, the Ni-Ti phase, the Co-Ti phase and the Cr phase and the dispersion distribution mode.
(4) Primary stretching: the primary stretching can also be called pre-stretching, along with the improvement of the pre-stretching deformation degree, the dislocation density is gradually increased, the deformation energy storage is increased, and larger kinetic energy is provided for later-stage aging precipitation. Generally, the stretch processing rate of the primary stretching is controlled to be more than 50%, and the aging precipitation process at the later stage can be effectively promoted.
(5) Primary aging: the alloy realizes a key process of precipitation strengthening, the high temperature is beneficial to complete crystallization of a structure and precipitation of a second phase, but the problems of precipitate coarsening, aggregation and overaging are easily caused when the temperature is too high, and the alloy has negative effects on the mechanical property of the alloy. The low-temperature aging is not beneficial to recrystallization of the alloy and precipitation of a second phase, and the precipitation strengthening effect of the alloy cannot be fully exerted. Therefore, the primary aging temperature of the alloy is controlled to be 300-500 ℃, and the heat preservation time is controlled to be 3-12 h. If the heat preservation time is too short, the solute in solid solution can not be fully precipitated; on the contrary, the heat preservation time is too long, the precipitated phase at the crystal boundary is obviously increased, the crystal grains are coarsened, and the mechanical property of the material is not improved.
(6) And (3) secondary stretching: the cold deformation is applied to the alloy after the primary aging, so that the strength of the alloy is further improved, and the processing rate of secondary stretching is controlled to be 10-80%.
(7) Secondary aging: the temperature of the secondary aging is generally lower than that of the primary aging, and the alloy is subjected to secondary aging treatment to further promote the precipitation of intermetallic compounds. Different secondary aging temperatures are selected according to the characteristics of the alloy, the selected temperature is controlled to be 200-350 ℃, and the heat preservation time is controlled to be 3-12 h.
In actual production, the stretching and aging times can be properly adjusted according to the specification requirements of products.
Compared with the prior art, the invention has the advantages that:
(1) according to the invention, the alloy element Mg and the alloy element X are added on the basis of the titanium bronze alloy with medium and low titanium contents, and the strength of the titanium bronze alloy with high titanium content can be realized by means of combining solution treatment and aging strengthening;
(2) the invention controls Cu2The Mg phase and the Fe-Ti phase, the Ni-Ti phase, the Co-Ti phase and the Cr phase are the same and dispersed to precipitate the phase synergistic effect, the content of solid solution titanium is reduced, and the conductivity of the titanium bronze alloy bar is further improved while the strength is influenced to the minimum extent;
(3) according to the invention, the softening temperature of the titanium bronze alloy is further raised by introducing the intermetallic compound with good high-temperature stability;
(4) the titanium bronze alloy bar can realize the tensile strength of more than 1000MPa, the electric conductivity of more than 15% IACS, the softening temperature of more than 500 ℃, has good comprehensive performance, and has obvious improvement on the comprehensive performance compared with the prior tin bronze.
(5) The alloy can be processed into bars, has good casting and processing characteristics, is suitable for large-scale industrialization, and provides good application prospects for the application of titanium bronze alloy bars in the industries of electronics, electricians, connectors, welding, heavy-duty machinery, hydraulic pressure and the like.
Detailed Description
The present invention will be described in further detail with reference to examples.
The titanium bronze alloys of examples 1 to 10 of the present invention and comparative example 3 were compounded in accordance with the compositions of the titanium bronze alloys in percentage by mass as listed in Table 1. The titanium bronze alloys of examples 1 to 10 and comparative example 3 of the present invention were subjected to melting, extrusion, solid solution, drawing and aging treatment by the following processes: controlling the temperature of a smelting furnace at 1300-1350 ℃ during smelting, carrying out iron mold casting, and making the ingot casting specification
The extrusion temperature of the cast ingot is 900-1000 ℃, and the cast ingot is extruded to the specification
Immediately and rapidly cooling the extruded blank to below 500 ℃ after extrusion, controlling the cooling speed to be above 300 ℃/s, and then cooling to below 50 ℃ at the cooling speed of 100-300 ℃/s; after extrusion, a solid solution process is adopted, the solid solution temperature is controlled to be 800-1000 ℃, the heat preservation time is 15-30 min, after heat preservation, the material is rapidly cooled, and the cooling speed is controlled to be more than 300 ℃/s; carrying out primary stretching and aging treatment after the solution treatment, wherein the primary stretching process comprises the following steps:
is stretched to
Aging treatment temperature 30Keeping the temperature for 3-12 h at 0-500 ℃; and then carrying out secondary stretching and aging treatment, wherein the secondary stretching process comprises the following steps:
is stretched to
The aging treatment temperature is 200-350 ℃, and the heat preservation time is 3-12 h.
In tables 1 and 2, comparative example 1 is a CuSn8 bar material with the same specification produced by a conventional process by using a CuSn8 brand component, comparative example 2 is a CuSn10 bar material with the same specification produced by a conventional process by using a CuSn10 brand component, comparative example 3 is a titanium bronze alloy bar material with the same specification conforming to a C19900 component, and comparative example 4 is a Cu-Ti-Mg alloy bar material with the same specification produced by a traditional secondary aging process.
The copper alloys of the examples and the comparative examples are tested according to the method specified by the relevant national and industrial standards
The tensile strength, elongation, conductivity, hardness, softening temperature, etc. of the bar samples are shown in Table 2.
Wherein, the room temperature tensile test is carried out according to GB/T228.1-2010 metallic material tensile test part 1: room temperature test method is carried out on an electronic universal mechanical property tester.
The conductivity is tested according to the GB/T3048-2007 electric wire and cable electrical property test method part 2: resistivity test of metallic material, expressed in% IACS.
Vickers hardness test is carried out on the cross section of the bar according to the point of the part 1 of the Vickers hardness test of GB-T4340.1-2009 metal material, namely the test method.
Softening resistance test the softening temperature of the sample was determined according to GB/T33370-2016 test method for the softening temperature of copper and copper alloys.
Alloys for each of examples and comparative examples
Analyzing precipitated phases in the microstructure of the cross section of the bar sample to obtain Cu2The ratio M/N of the total area of the Mg phase to the sum of the total areas of the Fe-Ti, Ni-Ti, Co-Ti and Cr phases and the individual area of less than 0.01 μ M2The results are shown in Table 2.
The performance test results prove that compared with the existing tin bronze CuSn8, CuSn10, high-titanium-content titanium bronze alloy and the traditional Cu-Ti-Mg alloy, the titanium bronze alloy bar has the comprehensive properties of excellent strength, conductivity, high-temperature softening resistance and the like.
TABLE 1 Components of examples 1 to 10 and comparative examples 1 to 4
TABLE 2 Performance test results of examples 1 to 10 and comparative examples 1 to 4
Claims (9)
1. The titanium bronze alloy bar is characterized by comprising the following components in percentage by mass: 1.5-2.5% of Ti, 0.01-0.5% of Mg, 0.01-1.0% of element X, and the balance of copper and inevitable impurities, wherein X is at least one element of Cr, Fe, Co and Ni.
2. The titanium bronze alloy bar according to claim 1, wherein the microstructure of the cross section of the titanium bronze alloy bar is Cu2The total area of the Mg phase is recorded as M, the sum of the total areas of the Fe-Ti phase, the Ni-Ti phase, the Co-Ti phase and the Cr phase is recorded as N, and the ratio of M to N is controlled to be 0.01-5.
3. The titanium bronze alloy bar according to claim 1, wherein the cross-section of the titanium bronze alloy barIn the microstructure of the cross section, the single area is less than 0.01 μm2The number of precipitated phases of (2) is more than 1X 106Per mm2。
4. The titanium bronze alloy bar according to claim 1, wherein the titanium bronze alloy bar has a tensile strength of 1000MPa or more and an electrical conductivity of 15% IACS or more.
5. The titanium bronze alloy bar according to claim 1, wherein the softening temperature of the titanium bronze alloy bar is greater than 500 ℃.
6. The titanium bronze alloy bar according to any of claims 1 to 5, wherein the titanium bronze alloy bar further comprises at least one element selected from the group consisting of B, Ce and Zr in an amount of 0.001 to 0.5% by mass in total.
7. The method for producing a titanium bronze alloy bar according to any of claims 1 to 6, comprising the steps of: fusion casting → extrusion → solid solution → stretching → primary aging → stretching → secondary aging.
8. The method of claim 7, wherein the extrusion temperature is 900 to 1000 ℃, the extruded billet obtained by extrusion is rapidly cooled to 500 ℃ or lower at a cooling rate of 300 ℃/s or higher, and then cooled to 50 ℃ or lower at a cooling rate of 100 to 300 ℃/s, the solid solution temperature after extrusion is 800 to 1000 ℃, the solid solution heat preservation time is 1 to 60min, and rapid cooling is performed after solid solution, wherein the cooling rate is 300 ℃/s or higher.
9. Use of a titanium bronze alloy bar according to any of claims 1 to 6 in the electronics, electrical engineering, connector, welding, heavy machinery, hydraulic industry.
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