CN116287855A - Aluminum bronze alloy and preparation method thereof - Google Patents

Aluminum bronze alloy and preparation method thereof Download PDF

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Publication number
CN116287855A
CN116287855A CN202211103617.7A CN202211103617A CN116287855A CN 116287855 A CN116287855 A CN 116287855A CN 202211103617 A CN202211103617 A CN 202211103617A CN 116287855 A CN116287855 A CN 116287855A
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mass
parts
alloy
blank
aluminum bronze
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Chinese (zh)
Inventor
赵丹
龙伟民
贾飞
张雷
刘鸣放
黎文强
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Henan Meikeyuan Wear Resisting Technology Co ltd
Ningbo Academy of Intelligent Machine Tool Co Ltd of China Academy of Machinery
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Henan Meikeyuan Wear Resisting Technology Co ltd
Ningbo Academy of Intelligent Machine Tool Co Ltd of China Academy of Machinery
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Priority to CN202211103617.7A priority Critical patent/CN116287855A/en
Publication of CN116287855A publication Critical patent/CN116287855A/en
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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
    • C22C9/05—Alloys based on copper with manganese as the next major constituent
    • 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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/001—Continuous casting of metals, i.e. casting in indefinite lengths of specific alloys
    • B22D11/004—Copper alloys
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/005—Continuous casting of metals, i.e. casting in indefinite lengths of wire
    • 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
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • C21D9/525—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length for wire, for rods
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/02—Making non-ferrous alloys by melting
    • 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
    • C22F1/02—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working in inert or controlled atmosphere or vacuum
    • 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

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Forging (AREA)

Abstract

The invention provides an aluminum bronze alloy and a preparation method thereof. Wherein the composition comprises the following components: mn: 10-15 parts by mass; al:7.7 to 8.5 parts by mass; fe:2.0 to 4.0 parts by mass; ni:2.0 to 4.0 parts by mass; re:0.04 to 0.08 parts by mass; cu:68.42 to 78.26 parts by mass; the alloy smelting process and Re element are carried out together. Wherein Re is La and Ce. In the technical scheme provided by the invention, the added Re element obviously refines grains, so that the grain structure compactness of the alloy material is effectively improved, and the performance is improved.

Description

Aluminum bronze alloy and preparation method thereof
Technical Field
The invention relates to the technical field of copper alloy welding wires, in particular to an aluminum bronze alloy and a preparation method thereof.
Background
Aluminum bronze alloys are mainly copper alloys with manganese as the main alloying element, of which the most representative and most widely used are aluminum bronze. The aluminum bronze plays a very important role in the mechanical industry, particularly when the aluminum content is about 8%, the aluminum bronze has good mechanical strength, wear resistance, seawater corrosion resistance and cold resistance, so that the aluminum bronze is widely applied to the fields of aerospace, ocean engineering, mine equipment and the like. However, the traditional cast aluminum bronze is easy to have defects such as internal shrinkage cavity, shrinkage porosity and the like; and when the Mn content is more than 10%, the high-manganese aluminum bronze is easy to generate a thermosensitive phenomenon, namely, the casting solidification structure grains are coarse, and the subsequent processing efficiency and the quality of a finished product of the aluminum bronze are very affected.
However, in the actual production process, there are problems in that: the horizontally continuously cast aluminum bronze rod is not subjected to grain refinement treatment, and the processing rate in the subsequent stretching process is low. Therefore, a new preparation method of the novel aluminum bronze alloy is newly developed, and has very important significance.
Disclosure of Invention
The invention aims to solve the problems that the horizontally continuous casting aluminum bronze bar is not subjected to grain refining treatment, and the processing rate in the subsequent stretching process is low.
Accordingly, embodiments of the present invention provide an aluminum bronze alloy comprising the following components: mn: 10-15 parts by mass; al:7.7 to 8.5 parts by mass; fe:2.0 to 4.0 parts by mass; ni:2.0 to 4.0 parts by mass; re:0.04 to 0.08 parts by mass; cu:68.42 to 78.26 parts by mass.
In the embodiment, mn is the main alloy element, and the higher the content is, the higher the strength and hardness of the alloy are, and the higher the wear resistance is; al is a main alloy element, the higher the content is, the higher the strength and hardness of the alloy are, and the better the corrosion resistance of the alloy is; fe is a main alloy element, and plays roles of refining copper alloy grains, improving strength and improving weldability with steel; ni is a main alloy element, so that the toughness and the impact resistance are improved, and the strength, the hardness, the thermal stability and the corrosion resistance of the copper alloy can be obviously improved; re as an additive can refine the grain structure of the copper alloy, improve the compactness of the grain structure and purify and remove impurities, thereby achieving the effects of improving the compactness, the machinability and the processing consistency of the grain structure of the alloy material.
Further, the Re element comprises La and Ce, wherein the mass ratio of La to Ce is 1:1.
in the implementation, re element is added, so that the as-cast columnar crystal structure can be eliminated, the effect of obviously refining grains is achieved, and the morphology of the metallographic structure of the alloy is changed, so that the effects of improving the hot processing performance of the alloy and the mechanical performance of the alloy at room temperature can be achieved, and the alloy is easier to stretch, extend and process at room temperature.
On the other hand, the invention also provides a preparation method of the aluminum bronze, which comprises the following steps:
s10: obtaining a metal raw material according to the mass parts, and carrying out mixed smelting and horizontal continuous casting to obtain a first blank;
s20: carrying out hot rotary forging on the first blank, and carrying out primary stretching treatment and annealing treatment to obtain a second blank;
s30: and carrying out secondary stretching treatment on the second blank to obtain the aluminum bronze alloy.
Further, in the preparation method, the smelting temperature of the mixed smelting is 1100-1380 ℃.
In the implementation, after high-temperature smelting and continuous casting, the internal impurities of the metal raw material are removed, a certain purification effect is achieved, and the crack defect caused by bending or straightening stress can be avoided by horizontal continuous casting, so that the first blank is obtained.
Further, in the preparation method, the first blank is subjected to hot rotary forging, wherein the incoming line temperature is more than or equal to 600 ℃, the outgoing line temperature is less than or equal to 150 ℃, and the rotary forging processing rate is less than or equal to 10%.
In the implementation, the bending strength of the blank is also improved because of the additional compressive stress on the surface of the forged piece after the rotary forging; in addition, the advantage of smooth surface after rotary forging can minimize the notch effect of the blank; so that the internal grains of the as-cast wire are further compact, and the casting defects such as shrinkage cavities, shrinkage cavities and the like in the as-cast wire are improved.
Further, in this production method, stretching is performed using a continuous drawing machine, and annealing is performed twice in a well type annealing furnace.
In the implementation, the processing rate between two times of annealing is not more than 40%, and the annealing temperature is controlled between 700 ℃ and 800 ℃, so that the grain structure is more compact.
Further, in the manufacturing method, the secondary stretching treatment uses a wire rod combined peeler for stretching, straightening and peeling treatment.
In the implementation, the yield of the blank is more than or equal to 95 percent.
Further, in the preparation method, the annealing process is always under the protection of inert gas.
In the implementation, the oxidation degree of the surface of the annealing material is effectively weakened due to the protection of inert gas.
Further, in the preparation method, a high-strength convection fan is arranged in the pit furnace.
In the implementation, the furnace atmosphere forms strong convection circulation due to the action of the high-strength convection fan, so that the temperature in the furnace is uniform, the temperature difference of each point is small, and the annealed material has uniform physical and mechanical properties.
In summary, the technical scheme provided by the invention has at least one of the following beneficial effects:
(1) The content of Mn and Al elements is increased, the strength and hardness of the alloy are obviously improved, and the corrosion resistance and wear resistance of the alloy are also stronger;
(2) The added Re element obviously refines grains, and effectively improves the grain structure compactness of the alloy material, thereby enhancing the tensile strength and the ductility of the alloy and being beneficial to improving the workability of the alloy;
(3) The online hot rotary forging is adopted, so that the crystal grains of the casting line blank are finer and denser, casting defects such as shrinkage cavity, shrinkage cavity and the like are improved, and the high-manganese aluminum bronze with specific specification is obtained by processing under relatively simple and stable processing conditions, thereby improving the processing efficiency and the quality of finished products and reducing the production cost;
(4) The alloy provided by the invention has excellent performance, obviously improves the tensile strength, also improves the hardness to some extent, and obviously improves the elongation.
Drawings
FIG. 1 shows as-cast solidification structures of example 1 and comparative example 1.
Detailed Description
In order that the above-recited objects, features and advantages of the present invention will become more apparent, a more particular description of embodiments of the invention will be rendered by reference to specific embodiments thereof which are illustrated in the appended drawings. All other embodiments, which can be made by those skilled in the art based on the embodiments of the invention without making any inventive effort, are intended to be within the scope of the invention.
In the related art, the existing material is not subjected to grain refinement treatment, so that the processing rate in the subsequent stretching process is low, and the casting defect treatment is not improved, so that the hardness is low and arc breakage easily occurs; accordingly, in view of the above problems, embodiments of the present invention provide a high manganese nickel-containing material comprising the following components Mn: 10-15 parts by mass; al:7.7 to 8.5 parts by mass; fe:2.0 to 4.0 parts by mass; ni:2.0 to 4.0 parts by mass; re:0.04 to 0.08 parts by mass; cu:68.42 to 78.26 parts by mass.
In the present embodiment, an aluminum bronze alloy is provided in which Mn and Al are main elements in the alloy, which improve the strength and hardness of the alloy and effectively improve the wear resistance and corrosion resistance; fe is a main alloy element, and plays roles of refining copper alloy grains, improving strength and improving weldability with steel; ni is a main alloy element, so that the toughness and the impact resistance are improved, and the strength, the hardness, the thermal stability and the corrosion resistance of the copper alloy can be obviously improved; re as an additive can refine the grain structure of the copper alloy and improve the compactness of the grain structure; on the other hand, the alloy material has the functions of purifying and removing impurities, thereby achieving the effects of improving the compactness, the machinability and the processing consistency of the grain structure of the alloy material.
Further, the Re element comprises La and Ce, wherein the mass ratio of La to Ce is 1:1
In the embodiment, the Re element La and Ce are added, so that the as-cast columnar crystal structure can be eliminated, the effect of obviously refining grains is achieved, and the metallographic structure of the alloy is changed, so that the effects of improving the hot processing performance of the alloy and the room-temperature mechanical performance can be achieved, and the alloy is easier to stretch, extend and process at room temperature.
On the other hand, the invention also provides a preparation method of the aluminum bronze alloy, which comprises the following steps:
s10: obtaining a metal raw material according to the mass parts, and carrying out mixed smelting and horizontal continuous casting to obtain a first blank;
s20: carrying out hot rotary forging on the first blank, and carrying out primary stretching treatment and annealing treatment to obtain a second blank;
s30: and carrying out secondary stretching treatment on the second blank to obtain the aluminum bronze alloy.
In the related art, the control of elements is difficult during the preparation, particularly Mn element is easy to volatilize during the preparation of alloy, so that the overall performance of the alloy is unstable; on the other hand, re element occupies less mass. Therefore, in order to balance the alloy properties, in this embodiment, according to step S10, each metal is first melted and a first billet is obtained by horizontal continuous casting. After the relatively stable first billet is obtained, the billet is subjected to hot swaging, drawing and annealing to obtain a second billet having a stronger stability in step S20. And finally, carrying out secondary stretching on the second blank to obtain the aluminum bronze alloy.
Further, in the preparation method, the smelting temperature of the mixed smelting is 1100-1380 ℃.
In the implementation, after high-temperature smelting and continuous casting, the internal impurities of the metal raw material are removed, a certain purification effect is achieved, and the crack defect caused by bending or straightening stress can be avoided by horizontal continuous casting, so that the first blank is obtained.
Further, in the preparation method, the first blank is subjected to hot rotary forging, wherein the incoming line temperature is more than or equal to 600 ℃, the outgoing line temperature is less than or equal to 150 ℃, and the rotary forging processing rate is less than or equal to 10%.
In the implementation, the bending strength of the blank is also improved because of the additional compressive stress on the surface of the forged piece after the rotary forging; in addition, the advantage of smooth surface after rotary forging can minimize the notch effect of the blank; so that the internal grains of the as-cast wire are further compact, and the casting defects such as shrinkage cavities, shrinkage cavities and the like in the as-cast wire are improved. Further, the alloy is always under the protection of inert gas in the heating, heat preservation and process.
Further, in this production method, stretching is performed using a continuous drawing machine, and annealing is performed twice in a well type annealing furnace.
In the implementation, the processing rate between two times of annealing is not more than 40%, and the annealing temperature is controlled between 700 ℃ and 800 ℃, so that the grain structure is more compact.
Further, in the manufacturing method, the secondary stretching treatment uses a wire rod combined peeler for stretching, straightening and peeling treatment.
In the implementation, the wire rod blank completes all the processes of stretching, modulating and peeling in the wire rod combined machine peeler, so that the raw material damage caused by carrying the wire rod blank for many times is prevented, and the yield of the blank is more than or equal to 95 percent and is qualified.
Further, in the preparation method, the annealing process is always under the protection of inert gas.
In the implementation, the principle that inert gas and metal are not easy to react to protect certain special metals is utilized to prevent the oxidation reaction from occurring in the heat treatment process and loss is caused, so that the oxidation degree of the surface of the annealing material is effectively weakened under the protection of the inert gas.
Further, in the preparation method, a high-strength convection fan is arranged in the pit furnace.
In the implementation, the furnace atmosphere forms strong convection circulation due to the action of the high-strength convection fan, so that the temperature in the furnace is uniform, the temperature difference of each point is small, and the annealed material has uniform physical and mechanical properties.
Example 1:
the aluminum bronze alloy of the present invention comprises the following components: mn:10.0 parts by mass of Al:7.7 parts by mass of Fe:2 parts by mass of Ni:2 parts by mass of La:0.02 parts by mass, ce:0.02 parts by mass, cu:78.2 parts by mass, the balance being unavoidable impurities, the sum of the component amounts being 100 parts by mass; a method for preparing an aluminum bronze alloy, comprising the steps of:
s10: alloy smelting and heat preservation are carried out on the components at 1250 ℃, and then a wire blank is formed by continuous casting on a horizontal continuous casting machine;
s20: carrying out on-line hot rotary forging on the wire blank to enable the internal grains of the as-cast wire rod to be further compact and improve casting defects such as shrinkage cavities and the like in the wire rod;
s30: stretching and annealing the wire blank on a continuous drawing machine and in a well type annealing furnace, wherein the processing rate between two times of annealing is 45%, the annealing temperature is 700 ℃, and the wire blank is processed to form a semi-finished product with smaller diameter;
s40: stretching, straightening and peeling the semi-finished wire rod in the step S3 on a wire rod combined peeler to form a finished wire rod with the yield of 94%;
s50: and (3) carrying out layer winding or barreling on the finished wire rod in the step S4.
Example 2:
the aluminum bronze alloy of the present invention comprises the following components: mn:12.0 parts by mass of Al:8 parts by mass of Fe:3 parts by mass of Ni:3 parts by mass of La:0.03 parts by mass, ce:0.03 parts by mass of Cu:73.9 parts by mass, the balance being unavoidable impurities, the sum of the component amounts being 100 parts by mass; a method for preparing an aluminum bronze alloy, comprising the steps of:
s10: alloy smelting and heat preservation are carried out on the components at 1300 ℃, and then a wire blank is formed by continuous casting on a horizontal continuous casting machine;
s20: carrying out on-line hot rotary forging on the wire blank to enable the internal grains of the as-cast wire rod to be further compact and improve casting defects such as shrinkage cavities and the like in the wire rod;
s30: stretching and annealing the wire blank on a continuous drawing machine and in a well type annealing furnace, wherein the processing rate between two times of annealing is 50%, the annealing temperature is 750 ℃, and the wire blank is processed to form a semi-finished product with smaller diameter;
s40: stretching, straightening and peeling the semi-finished wire rod in the step S3 on a wire rod combined peeler to form a finished wire rod with the yield of 96%;
s50: and (3) carrying out layer winding or barreling on the finished wire rod in the step S4.
Example 3:
the aluminum bronze alloy of the present invention comprises the following components: mn:14.0 parts by mass of Al:8.4 parts by mass of Fe:4 parts by mass of Ni:4 parts by mass of La:0.04 parts by mass, ce:0.04 parts by mass of Cu:69.5 parts by mass, the balance being unavoidable impurities, the sum of the component amounts being 100 parts by mass; a method for preparing an aluminum bronze alloy, comprising the steps of:
s10: alloy smelting and heat preservation are carried out on the components at 1350 ℃, and then a wire blank is formed by continuous casting on a horizontal continuous casting machine;
s20: carrying out on-line hot rotary forging on the wire blank to enable the internal grains of the as-cast wire rod to be further compact and improve casting defects such as shrinkage cavities and the like in the wire rod;
s30: stretching and annealing the wire blank on a continuous drawing machine and in a well type annealing furnace, wherein the processing rate between two times of annealing is 55%, the annealing temperature is 800 ℃, and the wire blank is processed to form a semi-finished product with smaller diameter;
s40: stretching, straightening and peeling the semi-finished wire rod in the step S3 on a wire rod combined peeler to form a finished wire rod with the yield of 97%;
s50: and (3) carrying out layer winding or barreling on the finished wire rod in the step S4.
Comparative example 1:
according to fig. 1, there is an as-cast solidification structure of example 1 and comparative example 1. Wherein, the graph a is an as-cast solidification structure of Cu7.7Al10Mn2Fe2Ni which is not subjected to on-line hot rotary forging treatment; FIG. b is an as-cast solidification structure of Cu7.7Al10Mn2Fe2Ni0.02Ce0.02La after on-line hot swaging treatment; figure c is an enlarged partial view of region a of figure b; and the graph d is the energy spectrum of the point A in the graph c.
From fig. 1, it is clear that the addition of the microalloying elements Ce and La, and the on-line hot rotary forging treatment, the as-cast structure of the aluminum bronze is significantly refined, and the grain size is reduced from 240 μm on average to 120 μm on average. On one hand, the reduction of the size of the as-cast crystal grains can improve the mechanical properties of the alloy such as tensile strength, hardness and the like through fine grain strengthening; on the other hand, the plastic deformation can be developed in more grains by increasing the number of grains in unit volume, so that dislocation accumulation is avoided, and the plasticity of the material is improved. In the present invention, the manner of grain refinement: 1. the grain boundary is nailed by microalloy elements, so that the grain boundary migration is blocked, and grains are refined; the alloy is dynamically recrystallized and the grains are refined through on-line hot rotary forging.
Comparative example 2:
the difference from example 2 is that Ce element was not added and the hot swaging treatment was not performed.
Comparative example 3:
the difference from example 1 is that Ce and La are not added and the hot rotary forging treatment is not performed.
Alloy sample wires were prepared in the same manner as in examples 1 to 3 and comparative examples 1 to 3, and each of the example and comparative example was cut out 3 wires of the same length as a test sample, and the test sample wires were tested in accordance with the following test items. The test results of the sample wires obtained by the same method are averaged, the test results are as follows
Table 1 shows:
test item Tensile Strength/Mpa Elongation/% Cladding layer hardness/HB
Example 1 680 36 175
Example 2 716 28 198
Example 3 758 24 225
Comparative example 1 630 33 162
Comparative example 2 670 24 173
Comparative example 3 705 19 197
Table 1 comparative results of example and comparative example sample wires
In FIG. 1, a is Cu 7.7 Al 10 Mn 2 Fe 2 As-cast solidification structure of Ni which is not subjected to on-line hot rotary forging treatment; b is Cu 7.7 Al 10 Mn 2 Fe 2 Ni 0.02 Ce 0.02 An as-cast solidification structure of La subjected to on-line hot rotary forging treatment, and a partial enlarged view of an area A in c; d is the energy spectrum of point A in c.
In conclusion, the test results of the examples 1-3 are all better than those of the comparative examples 1-3, which shows that the addition of La and Ce elements to the high-manganese nickel-containing wear-resistant and corrosion-resistant material and the addition of the online hot rotary forging process can effectively refine alloy grains and improve the compactness of grain structures, thereby enhancing the tensile strength and the ductility of the alloy and being beneficial to improving the workability of the alloy.
Finally, it should be noted that: the above embodiments are only for illustrating the technical solution of the present invention, and are not limiting; although the invention has been described in detail with reference to the foregoing embodiments, it will be understood by those of ordinary skill in the art that: the technical scheme described in the foregoing embodiments can be modified or some technical features thereof can be replaced by equivalents; such modifications and substitutions do not depart from the spirit and scope of the technical solutions of the embodiments of the present invention.

Claims (8)

1. An aluminum bronze alloy, characterized by comprising the following components:
mn: 10-15 parts by mass;
al:7.7 to 8.5 parts by mass;
fe:2.0 to 4.0 parts by mass;
ni:2.0 to 4.0 parts by mass;
re:0.04 to 0.08 parts by mass;
cu:68.42 to 78.26 parts by mass;
wherein the sum of the parts by mass of Mn, al, ni, fe is not less than 28 parts by mass, and the sum of the parts by mass of each component is 100 parts by mass.
2. The alloy of claim 1, wherein the Re element comprises La and Ce, wherein the mass ratio of La to Ce is 1:1.
3. a method of producing an aluminum bronze alloy as claimed in any one of claims 1 to 2, comprising the steps of:
s10: obtaining a metal raw material according to the mass parts, and carrying out mixed smelting and horizontal continuous casting to obtain a first blank;
s20: carrying out hot rotary forging on the first blank, and carrying out primary stretching treatment and annealing treatment to obtain a second blank;
s30: and carrying out secondary stretching treatment on the second blank to obtain the aluminum bronze alloy.
4. A process according to claim 3, wherein,
the smelting temperature of the mixed smelting is 1100-1380 ℃.
5. The method according to claim 3, wherein the hot swaging process parameters are:
the inlet wire temperature is more than or equal to 600 ℃, the outlet wire temperature is less than or equal to 150 ℃, and the rotary forging processing rate is less than or equal to 10%.
6. A method of manufacture according to claim 3, wherein the annealing temperature of the annealing treatment is 700 ℃ to 800 ℃.
7. A method of making as claimed in claim 3 wherein the secondary stretching treatment comprises:
the wire rod is combined with a peeler for stretching, straightening and peeling.
8. A process according to claim 3, wherein,
the primary stretching treatment adopts a continuous stretching machine; and/or
The annealing treatment adopts a well type annealing furnace.
CN202211103617.7A 2022-09-09 2022-09-09 Aluminum bronze alloy and preparation method thereof Pending CN116287855A (en)

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CN202211103617.7A CN116287855A (en) 2022-09-09 2022-09-09 Aluminum bronze alloy and preparation method thereof

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Application Number Priority Date Filing Date Title
CN202211103617.7A CN116287855A (en) 2022-09-09 2022-09-09 Aluminum bronze alloy and preparation method thereof

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Publication Number Publication Date
CN116287855A true CN116287855A (en) 2023-06-23

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