CN115927927B - High-magnesium-manganese-chromium-strontium-aluminum alloy and high-magnesium-manganese-chromium-strontium-aluminum alloy welding wire prepared from same - Google Patents
High-magnesium-manganese-chromium-strontium-aluminum alloy and high-magnesium-manganese-chromium-strontium-aluminum alloy welding wire prepared from same Download PDFInfo
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Classifications
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/20—Recycling
Abstract
The invention belongs to the technical field of aluminum alloy welding wires, and relates to a high-magnesium-manganese-chromium-strontium-aluminum alloy and a high-magnesium-manganese-chromium-strontium-aluminum alloy welding wire prepared by using the same. The high-magnesium manganese chromium strontium aluminum alloy comprises the following components in percentage by weight: magnesium: 4.5 to 5.5 weight percent; manganese: 0.05-0.20wt%; chromium: 0.05 to 0.09 wt.%; strontium: 0.011-0.05 wt%; titanium: 0.05 to 0.15 weight percent; boron: 0.0002 to 0.05 weight percent; beryllium: 0.0001 to 0.0005wt%; the balance of aluminum and unavoidable impurity elements; the content of the unavoidable impurity elements is less than 0.5wt%. The invention controls the surface hydrogen and the internal hydrogen of the welding material within certain and reasonable limits through the optimized design of the components, thereby meeting the force and electricity performance requirements of the welding material in welding process and service.
Description
Technical Field
The invention belongs to the technical field of aluminum alloy welding wires, and relates to a high-magnesium-manganese-chromium-strontium-aluminum alloy and a high-magnesium-manganese-chromium-strontium-aluminum alloy welding wire prepared by using the same.
Background
At present, the internationalization competition is increasingly serious in the key period of new and old kinetic energy conversion of the economy in China, and aluminum alloy are taken as important basic raw materials, so that the effect is particularly important. The aluminum and aluminum alloy processing materials are widely applied to the fields of electric power, traffic, construction, machinery, electronic information, aerospace, national defense and military industry and the like in the forms of pipes, rods, wires, plates, belts and foils, and play an indispensable role in protecting national economy construction, social development and the like.
In recent years, along with the trend of accelerating the optimization and upgrading steps of industrial structures and reducing energy consumption in China, policies of guidelines are gradually in deep focus, and along with the development of industries such as rail transit, automobile industry, rail transit and the like towards the light weight direction, the demands of high-performance aluminum and aluminum alloy welding wire products (hereinafter referred to as aluminum welding wires) are continuously increased.
In the development of more than ten years, the light weight equipment in China becomes the country with the most rapid progress in the world. The Chinese rail transit, new energy automobiles and tank trucks are gradually becoming a very inexhaustible strong force worldwide by means of learning, absorption, introduction, innovation and the like on the basis of independently researching, developing and tamping stamina, and the ever-growing economic and living needs of China are met in aspects.
The design application of the lightweight equipment can reduce the material cost, the manufacturing cost and the comfort of drivers and passengers, and is more energy-saving and environment-friendly. The lightweight design is mainly from the application of lightweight high-strength materials and the optimization design of the structure. The prior structure section is formed by extrusion welding of large hollow aluminum profiles, and the joint is long and regular, so that automatic operation is convenient to realize, and various automatic welding technologies are widely applied in the industry.
For a long time, most of welding wires used in the field of rail transit in China come from importation, especially in the field of rail transit in the field of public safety, especially in the field of high-speed rail with the speed per hour of more than 200 km, and 100% of aluminum alloy welding materials used are imported from western countries such as French, italy and the like.
On the other hand, according to statistics of related authorities, the sales volume of new energy automobiles in China reaches incredible 500 ten thousand in 2023 years, and the sales volume is continuously increased later, and the aluminum alloy welding materials of key parts on the new energy automobiles also depend on import from Europe and America, so that the new energy automobile industry in China is seriously hindered from running own characteristic development roads.
The domestic aluminum alloy raw material smelting and brightening surface treatment process is lagged, and only low-end aluminum welding wires can be produced at present, are used for welding in non-critical structure and high performance, and cannot meet the welding manufacturing requirements of high-end equipment. Therefore, in order to meet the manufacturing requirements of high-end equipment in China, the localization of high-end aluminum welding wires and the development of patent products with independent intellectual property rights are urgently needed.
The welding performance of the aluminum alloy structural part is mainly dependent on the welding process and the stability of the alloy composition and performance of the welding material under the condition of certain base materials. Wherein the welding material is an important factor affecting the metal composition, structure and heat cracking property of the base metal in the near-seam area of the welding seam, and the corrosion resistance and mechanical property of the welding seam. Meanwhile, in order to meet the requirements of the automatic MIG welding of the robot, the process stability in the welding process is guaranteed, higher requirements are put on the aluminum alloy welding material, and the automatic tray welding material of the robot is required to be fine in size, bright and clean in surface and has certain rigidity. Therefore, the high-level development of light-weight equipment in China is urgent to independently develop high-quality aluminum alloy welding materials.
On the other hand, aluminum alloy welding materials are key to aluminum and aluminum alloy inert gas shielded arc welding, and high quality aluminum welding wires are required to obtain excellent welding quality, so that not only is preferable component design required, but also optimized preparation process design is required. Compared with imported welding wires, the domestic welding wires have the defects of low strength of welded joints, more internal pores and inclusions, poor stability of the welding wires, poor surface quality and the like.
The high-end aluminum alloy welding material depends on import for a long time, an intangible and tangible industrial chain is formed in China, a matching relation is formed between the high-end aluminum alloy welding material and the imported welding material in terms of welding equipment, welding tools and the like, and an intangible matching relation is formed between the high-end aluminum alloy welding material and the imported welding wire in terms of welding technology and welding methods, so that the high-end aluminum alloy welding material is better in replacement of import and is automatically controllable, and therefore aluminum alloy welding materials (aluminum welding wires) manufactured by later-entering manufacturers have good matching performance with the welding equipment, the welding tools and the welding technology.
The main technical conditions of the aluminum welding wire at home and abroad are described as follows:
(1) Component aspect
The traditional aluminum welding wire applied to the field of light-weight high-end equipment is the most widely applied 5XXX aluminum magnesium alloy welding wire, the typical brands of the aluminum welding wire are ER5356 and ER5087, the problems of lower welding strength, thick weld joint structure and the like exist in the using process, at present, the aluminum welding wire is refined by adding Sc in China to improve the strength of the weld joint, but the aluminum magnesium alloy after the Sc is added has poor processability, and the aluminum welding wire cannot be applied to industrial manufacturing at present, such as patent CN103286471B; there are improvements in weld strength by increasing Mg content and Zn element, as in patent CN103286472B.
On the other hand, according to ISO 18273-2015 international standards: other 5XXX series aluminum magnesium alloy welding wires, such as Al5356 and Al5356, generally have a Mg content of greater than 4.5wt%, and under non-vacuum conditions, because the metal vapor pressure of Mg is relatively low, the volatilization of Mg during smelting is relatively high, so that the proportion of Mg added is much higher than that of conventional other metals in order to ensure that the components of Mg meet the standard requirements, or a special smelting method is adopted, thus leading to the increase of the cost during actual production.
(2) In the aspect of preparation technology
The foreign aluminum welding wire is generally manufactured by the following method:
smelting, continuous casting and rolling phi 9.5, multi-pass wire drawing (including multi-pass annealing), and finished product.
The process can obtain phi 9.5 parent rod with large ladle weight and even and fine structure, thereby further obtaining the aluminum welding wire finished product with higher and more stable quality. There are also domestic studies on continuous casting and rolling processes, such as patent CN106244861a. However, the specification of the master rod after hot rolling is phi 9.5mm, the specification of the common welding wire is phi 1.2mm, the subsequent processing flow is long, and the stability of the process is difficult to guarantee.
The domestic aluminum welding wire is generally manufactured by the following two processes:
(1) smelting, horizontal continuous casting phi 9.5, multi-pass wire drawing (including multi-pass annealing), and finished product;
the process is characterized by comprising the following steps: firstly, the effective melt on-line treatment cannot be carried out, more impurities are contained in the wire rod, and the hydrogen content is high, so that the defects of air holes, impurities and the like of welding seams during welding are caused, and the welding quality is affected; secondly, the phi 9.5 master rod produced by the process method is an as-cast structure, and has more casting defects in the master rod, such as large-particle compounds, looseness, holes and other casting defects, and the casting defects of the master rod cannot be eliminated only by multi-pass stretching, and the defects can influence the welding process and the weld quality. Therefore, the process can only produce low-end aluminum welding wires.
(2) Smelting, semi-continuous casting, extrusion phi 9.5, multi-pass wire drawing (including multi-pass annealing) and finished product;
the process is characterized by comprising the following steps: because the weight of each coil of the master rod is not more than 100kg under the influence of the length of the extruded ingot, each coil of wire is required to be connected together before the subsequent stretching, and excessive joints not only consume time, but also have different properties of the wire joints and wires, so that the overall consistency of the wires is affected; meanwhile, due to the limitation of the extrusion process, coarse grain structure is generated on the surface of the blank due to the fact that the extrusion temperature is too high in the extrusion process, the subsequent processing is difficult to eliminate, and the coarse grain structure remained on the surface layer of the welding wire is harmful to the gold melting performance. Therefore, the process is only suitable for the production of small-batch or sample products, and is not suitable for the production of large-scale aluminum welding wires in batches.
The domestic welding wire cannot meet the requirements of the aluminum alloy welding material for high-end equipment in the aspects of welding wire performance consistency and welding wire linear stability due to the limitations of the process, the storage condition of the welding material and the production condition, so that a new technology is urgently needed to be researched to meet the MIG welding requirements in the high-end field.
Disclosure of Invention
Aiming at the defects in the prior art, the invention provides the high-magnesium-manganese-chromium-strontium-aluminum alloy and the high-magnesium-manganese-chromium-strontium-aluminum alloy welding wire prepared by using the same, and the surface hydrogen and the internal hydrogen of the welding material are controlled within certain and reasonable limits through the optimal design of components and advanced hydrogen removal and hydrogen control processes, so that the force and electricity performance requirements of the welding material in welding process and service are met.
One object of the invention is achieved by the following technical scheme:
the high-magnesium manganese chromium strontium aluminum alloy comprises the following components in percentage by weight:
magnesium: 4.5 to 5.5 weight percent; manganese: 0.05-0.20wt%; chromium: 0.05 to 0.09 wt.%; strontium: 0.011-0.05 wt%; titanium: 0.05 to 0.15 weight percent; boron: 0.0002 to 0.05 weight percent; beryllium: 0.0001 to 0.0005wt%; the balance of aluminum and unavoidable impurity elements; the content of the unavoidable impurity elements is less than 0.5wt%.
In order to ensure the surface roughness and the stability of the mechatronic performance of the welding wire and meet the arc stability requirement of MIG welding, the impurity elements of the welding material are defined as follows according to the material characteristics: the impurity element includes: less than or equal to 0.020wt% of Pb, less than or equal to 0.015wt% of Sb, less than or equal to 0.015wt% of Bi, less than or equal to 0.015wt% of Te, less than or equal to 0.20wt% of Si, less than or equal to 0.25wt% of Fe, less than or equal to 0.015wt% of Ni, less than or equal to 0.005wt% of Ba, less than or equal to 0.015wt% of Zr, less than or equal to 0.015wt% of Ga, less than or equal to 0.015wt% of P, less than or equal to 0.015wt% of V, less than or equal to 0.005wt% of Ce, less than or equal to 0.0005wt% of Li, less than or equal to 0.0020wt% of Na, and less than or equal to 0.0030wt% of Ca.
Meanwhile, in order to improve the service performance of the welding seam under the extremely cold and extremely hot condition, the impurity element of the high-magnesium manganese chromium strontium aluminum alloy is less than or equal to 0.0040wt% of Li+Na+Ca.
Another object of the invention is achieved by the following technical solutions:
a preparation method of a high-magnesium-manganese-chromium-strontium-aluminum alloy welding wire comprises the following steps: and (3) preparing materials, smelting, continuously casting and rolling according to the components of the high-magnesium manganese chromium strontium aluminum alloy to obtain a master rod, performing plastic processing, annealing, plastic deformation, peeling and split charging on the master rod.
And (3) batching: aluminum and magnesium are added in the form of pure metal, other additive elements are added in the form of aluminum-based intermediate alloy, and the aluminum and magnesium are prepared according to the weight percentage of the formula;
smelting and melt processing: the alloy smelting temperature is preferably 670-760 ℃, and the alloy is subjected to online degassing, refining and filtering after being melted to reduce hydrogen, alkali metal elements and impurity particles in the melt, wherein a casting process in continuous casting and rolling adopts a method of adding chloride and chlorine for refining;
preferably, the smelting process adopts a mode of adding rare earth in a smelting furnace to perform online dehydrogenation treatment;
further preferably, the rare earth is lanthanide rare earth, and is added in a mode of intermediate alloy;
further preferably, the addition amount of the rare earth is 0.05-0.35% of the mass of the melt;
continuous casting and rolling to obtain a master rod: the continuous casting temperature is preferably 680-750 ℃, the hot rolling temperature is preferably 370-420 ℃, and the specification of the rolled aluminum alloy master rod is preferably phi 3.5-phi 6.5;
plastic working of a master rod: plastic processing is carried out on the prepared bus bar to obtain an aluminum alloy bus, wherein the specification of the bus bar is preferably phi 2.0-phi 4.0mm;
annealing: recrystallizing and annealing the prepared bus, wherein the annealing temperature is preferably 370-480 ℃ and the time is preferably 8-18.0 hours;
plastic deformation: the bus bar thus produced is subjected to plastic deformation at a large working rate, preferably more than 65% and less than 85%, to obtain an aluminum alloy pre-formed blank.
Peeling and subpackaging: peeling the blank before forming the aluminum alloy, wherein the peeling thickness is preferably 0.01-0.15 mm, obtaining a finished product of the high-magnesium manganese chromium strontium aluminum alloy welding wire, the specification is preferably phi 0.8-phi 2.0mm, and then subpackaging the finished products of the aluminum welding wire with different weights according to different requirements of customers.
Preferably, in the preparation process of the invention, after peeling and subpackaging to obtain a high magnesium manganese chromium strontium aluminum alloy welding wire finished product, low-temperature step annealing is performed, wherein the low-temperature step annealing is as follows: the annealing temperature is 50-135 ℃, and the heat preservation is carried out for 3-24 hours at the annealing temperature; in the low-temperature step annealing process, the temperature rising speed is 25-35 ℃/h at the temperature lower than 50 ℃ and is 5-15 ℃/h at the temperature higher than 50 ℃.
Another object of the invention is achieved by the following technical solutions:
the high-magnesium-manganese-chromium-strontium-aluminum alloy welding wire is prepared by the preparation method.
Preferably, the diameter of the high-magnesium-manganese-chromium-strontium-aluminum alloy welding wire is phi 0.8-phi 2.0mm, and the hydrogen content of the high-magnesium-manganese-chromium-strontium-aluminum alloy welding wire is less than 5.30ppm.
Preferably, the spring-open diameter of the high-magnesium-manganese-chromium-strontium-aluminum alloy welding wire is phi 350-phi 650mm, and the warping is less than 20mm.
Preferably, the tensile strength of the high-magnesium-manganese-chromium-strontium-aluminum alloy welding wire is 400-480 Mpa, and the welding strength is not lower than 0.63 times of the welding wire strength.
Compared with the prior art, the invention has the following beneficial effects:
(1) The invention controls the Mg content to be 4.5-5.5wt percent so as to play the following roles:
(1) mg has remarkable strengthening effect, the solid solubility of Mg in aluminum is very large, and Mg is taken as Mg from an Al matrix in the solidification process 3 Al 2 The phase is precipitated and uniformly distributed in the Al matrix, so as to play a role in precipitation strengthening;
(2) the Mg content can reduce the plasticity of the material while increasing the strength of the material, but the Mg element is easy to be unevenly distributed.
(2) The invention refines grains by adding Sr element and carries out modification treatment on alpha-Al. The melting point of Sr is about 769 ℃, the crystal structure belongs to a body-centered cubic lattice structure, and the Sr can react with water at normal temperature. The invention adopts the mode of adding the Al-Sr intermediate alloy before casting, and the temperature of adding the Al-Sr intermediate alloy cannot exceed 760 ℃. Summary of experimental studies according to the invention iteration found that the addition of Sr has the following benefits on melt quality:
(1) sr can enable the grain boundary of alpha-Al to be smoother, the macroscopic performance of the material is more stable, the fatigue resistance is better, and the impurity phase Mg is hindered 2 Excessive growth and aggregation of Si in solid solution, and reduction of Mg 2 The harm of Si to the material organization property;
(2) sr can react with the elemental hydrogen in the melt to produce strontium hydride (SrH) 2 ) Has the effect of removing hydrogen.
Sr+H 2 ＝SrH 2 。
(3) Because the chemical property of Sr is more active than Al, sr can react with oxygen simple substance in melt to generate strontium oxide (SrO), thereby reducing Al in solid solution 2 O 3 Producing and purifying the melt.
2Sr+O 2 ＝2SrO。
(3) According to the invention, a certain amount of B element is added to improve the grain refinement effect of Ti, improve the nucleation rate of Ti element in crystal and reduce the precipitation of impurity element in crystal boundary, and meanwhile, B also has the following effects:
(1) because aluminum and aluminum alloys are very prone to absorb/adsorb water in the air, when aluminum is smelted, the water is decomposed into hydrogen and oxygen, and if a special treatment mode is not adopted, the oxygen and hydrogen remained in the melt can greatly reduce the mechanical properties of the material. The invention reduces the deficiency through the addition of B, the B can react with oxygen at the temperature of more than 400 ℃, the oxygen content in the melt is reduced, and the mechanical property of the material is improved;
(2) TiB formation at grain boundaries during casting solidification 2 The hard phase is used as hard particles to produce pinning effect on dislocation, so that dislocation movement is hindered, and the deformation resistance of the alloy is improved;
(3) further eliminating the harm of Li, na, ca, K and other metals, because of TiB 2 The effect of grain refinement is that the metal is dissolved in alpha grains in the form of metal atoms, so that the segregation of Li, na, ca, K at grain boundaries is reduced, and the mechanochemical performance of the material is reduced.
(4) According to the invention, by controlling the mass percentage of the main element Be to Be 0.0001-0.0005 wt%, a layer of Be film is formed on the surface of the melt by the Be, the melt is protected from further oxidation, and the burning loss of the elements easy to burn such as Mg, sr, re and the like in the smelting process is reduced.
(5) According to the invention, chlorine salt or chlorine refining agent is added to react with alkali metal elements Li, na and Ca to generate corresponding compounds so as to reduce the content of corresponding elements in the melt, and the limit value is set as follows: ce is less than or equal to 0.005wt%, li is less than or equal to 0.0005wt%, na is less than or equal to 0.0020wt% and Ca is less than or equal to 0.0030wt%, so that the performance of the material is not affected significantly.
(6) The impurity elements such as less than or equal to 0.020wt% of Pb, less than or equal to 0.015wt% of Bi, less than or equal to 0.015wt% of Te, less than or equal to 0.20wt% of Si, less than or equal to 0.25wt% of Fe, less than or equal to 0.015wt% of Ni, less than or equal to 0.005wt% of Ba, less than or equal to 0.015wt% of Zr, less than or equal to 0.015wt% of Ga, less than or equal to 0.015wt% of P, less than or equal to 0.015wt% of V and the like are determined, and the impurity elements are used for limiting the types of aluminum ingots and intermediate alloys selected for manufacturing the aluminum alloy welding wire, so that the physical and chemical properties of the welding wire are not influenced by raw material impurities, and the alloy performance is reduced.
(7) The invention adopts a continuous casting and rolling mode to produce the phi 3.5-phi 6.5 aluminum alloy master rod, and the method has high production efficiency, uniform and fine product structure and stable quality. Compared with the horizontal continuous casting process, the internal air holes and inclusions are fewer; compared with the extrusion process, the method has the following advantages:
(1) the large-package heavy parent rod with stable performance can be obtained, the coil weight is up to 2 tons, each package does not need to be connected together for production, no connection point exists in the final product, and meanwhile, the time for connecting the parent rod is saved, and the efficiency is improved;
(2) taking ER5356 master rod manufacturing as an example, the continuous casting and rolling line speed is more than 4.5m/s, while the extrusion line speed of extruding phi 9.5 master rods is about 0.3m/s, and meanwhile, the extrusion process also has feeding and discharging time, so the continuous casting and rolling mode adopted by the invention has great improvement on the production efficiency.
(3) Compared with foreign continuous casting and rolling processes: the specification of the master rod after rolling is smaller, the processing pass required for subsequent processing to the finished product specification is correspondingly shortened, and meanwhile, because the rolling specification is smaller, the corresponding rolling and casting equipment is smaller in size, the equipment investment and occupied space are smaller, and the production cost and the equipment investment cost are lower.
(8) The invention adds Re with the addition proportion of 0.05-0.35% of the mass of the melt, and forms stable compounds such as ReH with hydrogen in the melt 2 Has the effect of controlling hydrogen.
(9) The finished welding wire manufactured by the invention adopts a low-temperature step annealing system, the internal stress of the welding wire is fully released, the second phase of the material is fully separated out, the chemical components in and among crystals are more stable, the appearance is that the coil diameter and the warpage of the welding wire are more stable, the requirements of MIG welding on wire feeding property and the stability of the rod length during welding are met, and the forming property and the welding manufacturability of the welding wire during welding are ensured.
(10) The low-temperature step annealing system is adopted, so that the welding wire is remelted and resolidified to form a second phase in a weld joint structure when in welding application, wherein the adopted Mn, cr, sr and Ti elements can form the second phase preferentially in the resolidification process and are dispersed and distributed in a weld joint melt to serve as crystal nuclei to promote the internal nucleation of liquid metal in the weld joint, so that the effect of refining weld joint structure grains is achieved.
Drawings
FIG. 1 is a schematic diagram of the structure of the high-magnesium Mn-Cr-Sr-Al alloy of the present invention;
in the figure: 1: alpha-Al; 2: mg of 2 Si；3：Al 4 Sr；4：(Fe,Mn,Cr)Al x ；5:Mg 3 Al 2 ；6:Ti 2 B。
Detailed Description
The technical solution of the present invention will be further described by means of specific examples and drawings, it being understood that the specific examples described herein are only for aiding in understanding the present invention and are not intended to be limiting. And the drawings described herein are for illustration purposes only and are not intended to limit the scope of the present disclosure. Unless otherwise indicated, all materials used in the examples of the present invention are those commonly used in the art, and all methods used in the examples are those commonly used in the art.
The following are definitions of some terms of the invention:
the intermediate alloy disclosed by the invention refers to: the metal is used as matrix, and one or more simple substances are added into the matrix to solve the problems of easy burning loss, difficult melting of high melting point, segregation of density da Yi and the like of the simple substances or special alloy for improving the alloy performance, so that the metal is an additive type functional material.
The melt processing of the invention is as follows: removing harmful substances such as gas, impurities, alkali metal elements and the like in the melt by means of gas, refining agent, filtration and the like, so that the melt is purified.
The alkali metal element in the invention refers to: six metallic elements of group IA in the periodic Table of elements other than hydrogen (H), namely lithium (Li), sodium (Na), potassium (K), rubidium (Rb), cesium (Cs). The alkali metals all have an outermost electron belonging to s-orbit, and the chemical properties of the alkali metals show very obvious homologous behaviors.
The precipitation strengthening refers to hardening caused by dispersion distribution of solute atoms in a supersaturated solid solution and/or dissolved particles in a matrix. It is reinforced by precipitation of dispersed second phase precipitate particles which can also block dislocation movement.
The modification treatment of the invention is as follows: a small amount of active substances are added into the molten metal to promote the nucleation of the inside of the liquid metal or change the crystal growth process, so as to obtain fine casting grains, thereby achieving a method for improving the material performance. The modifier commonly used in the production comprises a nucleation modifier and an adsorption modifier. The nucleation modifier has the action mechanism that substances capable of generating non-spontaneous crystal nuclei are added into the aluminum melt, so that the purpose of grain refinement is achieved through heterogeneous nucleation in the solidification process. The adsorption modifier is characterized in that the adsorption modifier is enriched on a phase interface during crystal growth to prevent the crystal from growing, and can form larger supercooling components, so that the crystal branches to form thin necking to be easy to fuse, and the free of the crystal and the increase of crystal nuclei are promoted.
The linearity of the welding wire comprises the diameter of the welding wire in a free state, the torsion degree (English is Helix) of the welding wire in a natural flattening state, and the torsion is replaced by a warping index in the invention, namely the height of one end of the welding wire, which is in the free state, from a horizontal plane in the natural flattening state when the length of the welding wire cut out a circumference, and the degree of releasing the compressive stress of the welding wire after the welding wire is processed. The degree of compressive stress relief is characterized in terms of engineering practice in terms of the value of the change in yield strength that is invented.
The alloy of the invention refers to pure welding state metal, and the alloy performance refers to mechanical properties of alloy, including tensile strength, yield strength, elongation and the like.
The continuous casting and rolling of the invention means: and (3) casting the molten metal into a casting blank through a casting wheel, and rolling the casting blank into a round rod with a certain diameter when the round rod directly passes through a rolling mill connected with a casting machine.
The Mpa of the invention is: the pressure unit megapascals is used for representing the tensile strength or the yield strength of the material.
In order to prove that the high-magnesium-manganese-chromium-strontium-aluminum alloy composition used for the high-magnesium-manganese-chromium-strontium-aluminum alloy welding wire and the preparation method are favorable, the high-magnesium-manganese-chromium-strontium-aluminum alloy composition is proved by the following examples.
Example 1
The chemical compositions and mass percentages of the high-magnesium manganese chromium strontium aluminum alloy of the embodiment are shown in table 1, and the content of unavoidable impurity elements is less than 0.5% wt.
The preparation method of the high-magnesium-manganese-chromium-strontium-aluminum alloy welding wire comprises the following steps:
(1) Raw material proportioning: preparing materials according to the components of the high-magnesium manganese chromium strontium aluminum alloy, and preparing 6 tons of alloy according to chemical component requirements by adopting industrial pure aluminum, industrial pure magnesium and intermediate alloys of Al-Mn, al-Cr, al-Sr, al-Ti and Al-Ti-B, al-Be as raw materials;
(2) Smelting and melt processing: the prepared raw materials are smelted, the alloy smelting temperature is 730 ℃, and the alloy is subjected to online degassing, refining and filtering after being smelted so as to reduce hydrogen, alkali metal elements and impurity particles in the melt, wherein a casting process in continuous casting and rolling adopts a method of adding chloride and chlorine for refining; rare earth La is added to one side of the alloying furnace at the joint of the chute and the alloying furnace, and the addition amount is 0.06% of the weight of the melt;
(3) Cogging is carried out by continuous casting and rolling, the continuous casting temperature is 700 ℃, the hot rolling temperature is 380 ℃, and the specification phi of the rolled aluminum alloy master rod is 6.1.
(4) Plastic working: carrying out plastic processing on the master rod prepared in the step (3) to obtain an aluminum alloy bus with the specification of phi 2.75;
(5) Annealing: recrystallizing and annealing the bus prepared in the step (4) at 375 ℃ for 10.0 hours;
(6) Plastic deformation: carrying out plastic deformation with large processing rate on the bus manufactured in the step (5) to obtain a blank before forming an aluminum alloy, wherein the processing rate is 78.5%;
(7) Peeling and split charging of blanks before aluminum alloy forming: peeling the blank before forming the aluminum alloy, which is prepared in the step (7), wherein the peeling thickness is 0.05mm, and the specification of a welding wire finished product is phi 1.2;
(8) Step annealing is carried out on the final product, the furnace gas pressure of an annealing furnace for step annealing is controlled at 1 atmosphere, and the annealing temperature is as follows: the temperature is 70 ℃ and the heat preservation time is 7 hours; the heating rate is 30 ℃/h at less than 50 ℃, and the heating rate is 10 ℃/h at more than 50 ℃.
The high-magnesium manganese chromium strontium aluminum alloy welding wires prepared according to the steps (1) - (8) have the following properties:
1) The hydrogen content of the finished wire was 2.5ppm.
2) The spring-open diameter of the welding wire is phi 560, and the warping is 8mm.
3) The tensile strength of the high-magnesium-manganese-chromium-strontium-aluminum alloy welding wire is 435Mpa.
Example 2
The components and contents of the high magnesium-manganese-chromium-strontium-aluminum alloy welding wire of example 2 are shown in table 1, and the preparation method of the high magnesium-manganese-chromium-strontium-aluminum alloy welding wire of example 2 is the same as that of example 1.
The prepared high-magnesium manganese chromium strontium aluminum alloy welding wire has the following properties:
1) The hydrogen content of the finished wire was 1.8ppm.
2) The spring-open diameter of the welding wire is phi 520, and the warping is 4mm.
3) The tensile strength of the high-magnesium-manganese-chromium-strontium-aluminum alloy welding wire is 445Mpa.
Example 3
The components and contents of the high magnesium-manganese-chromium-strontium-aluminum alloy welding wire of example 3 are shown in table 1, and the preparation method of the high magnesium-manganese-chromium-strontium-aluminum alloy welding wire of example 3 is the same as that of example 1.
The prepared high-magnesium manganese chromium strontium aluminum alloy welding wire has the following properties:
1) The hydrogen content of the finished wire was 1.6ppm.
2) The spring-open diameter of the welding wire is phi 600, and the warp is 7mm.
3) The tensile strength of the high-magnesium-manganese-chromium-strontium-aluminum alloy welding wire is 440Mpa.
Example 4
The chemical compositions and mass percentages of the high-magnesium-manganese-chromium-strontium-aluminum alloy of the embodiment are shown in table 1, and the content of the unavoidable impurity elements is less than 0.5wt%.
The preparation method of the high-magnesium-manganese-chromium-strontium-aluminum alloy welding wire comprises the following steps:
(1) Raw material proportioning: preparing materials according to the components of the high-magnesium manganese chromium strontium aluminum alloy, and preparing 6 tons of alloy according to chemical component requirements by adopting industrial pure aluminum, industrial pure magnesium and intermediate alloys of Al-Mn, al-Cr, al-Sr, al-Ti and Al-Ti-B, al-Be as raw materials;
(2) Smelting and melt processing: the prepared raw materials are smelted, the alloy smelting temperature is 740 ℃, and the alloy is subjected to online degassing, refining and filtering after being smelted so as to reduce hydrogen, alkali metal elements and impurity particles in the melt, wherein a casting process in continuous casting and rolling adopts a method of adding chloride and chlorine for refining; rare earth Ce is added to one side of the alloying furnace at the joint of the chute and the alloying furnace, and the addition amount is 0.09% of the weight of the melt;
(3) Cogging is carried out by continuous casting and rolling, the continuous casting temperature is 710 ℃, the hot rolling temperature is 390 ℃, and the specification phi of the rolled aluminum alloy master rod is 6.15.
(4) Plastic working: carrying out plastic processing on the master rod prepared in the step (3) to obtain an aluminum alloy bus with the specification of phi 3.2;
(5) Annealing: recrystallizing and annealing the bus prepared in the step (4) at 370 ℃ for 12.0 hours;
(6) Plastic deformation: carrying out plastic deformation with large processing rate on the bus manufactured in the step (5) to obtain a blank before forming an aluminum alloy, wherein the processing rate is 73.5%;
(7) Peeling and split charging of blanks before aluminum alloy forming: peeling the blank before forming the aluminum alloy, which is prepared in the step (7), wherein the peeling thickness is 0.06mm, and the specification of a welding wire finished product is phi 1.6;
(8) Step annealing is carried out on the final product, the furnace gas pressure of an annealing furnace for step annealing is controlled at 1 atmosphere, and the annealing temperature is as follows: the temperature is 75 ℃ and the heat preservation time is 6 hours; the heating rate is 30 ℃/h at less than 50 ℃, and the heating rate is 10 ℃/h at more than 50 ℃.
The high-magnesium manganese chromium strontium aluminum alloy welding wires prepared according to the steps (1) - (8) have the following properties:
1) The hydrogen content of the finished wire was 3.5ppm.
2) The spring-open diameter of the welding wire is phi 570, and the warp is 12mm.
3) The tensile strength of the high-magnesium-manganese-chromium-strontium-aluminum alloy welding wire is 430Mpa.
Example 5
The components and contents of the high magnesium-manganese-chromium-strontium-aluminum alloy welding wire of example 5 are shown in table 1, and the preparation method of the high magnesium-manganese-chromium-strontium-aluminum alloy welding wire of example 5 is the same as that of example 4.
The prepared high-magnesium manganese chromium strontium aluminum alloy welding wire has the following properties:
1) The hydrogen content of the finished wire was 3.6ppm.
2) The spring-open diameter of the welding wire is phi 550, and the warping is 6mm.
3) The tensile strength of the high-magnesium-manganese-chromium-strontium-aluminum alloy welding wire is 425Mpa.
Example 6
The components and contents of the high magnesium-manganese-chromium-strontium-aluminum alloy welding wire of example 6 are shown in table 1, and the preparation method of the high magnesium-manganese-chromium-strontium-aluminum alloy welding wire of example 6 is the same as that of example 4.
The prepared high-magnesium manganese chromium strontium aluminum alloy welding wire has the following properties:
1) The hydrogen content of the finished wire was 3.0ppm.
2) The spring-open diameter of the welding wire is phi 520, and the warping is 5mm.
3) The tensile strength of the high-magnesium-manganese-chromium-strontium-aluminum alloy welding wire is 428Mpa.
The chemical compositions and contents of the high magnesium manganese chromium strontium aluminum alloys of comparative examples 1-9 are shown in Table 1, respectively. The preparation method of the high-magnesium manganese chromium strontium aluminum alloy welding wires of comparative examples 1-4 is the same as that of example 1; the preparation method of the high-magnesium-manganese-chromium-strontium-aluminum alloy welding wires of comparative examples 4 to 8 is the same as that of example 4, and the preparation method of the high-magnesium-manganese-chromium-strontium-aluminum alloy welding wire of comparative example 9 is different from that of example 1 in that the peeled and split-packed product of comparative example 9 is not subjected to step annealing.
Table 1 chemical composition tables of examples 1 to 6 and comparative examples 1 to 9 of high magnesium manganese chromium strontium aluminum alloys
TABLE 2 welding wire properties and weld properties for example 1 and comparative examples 1-6
In addition, because the Zr content in the comparative example 1 is too high, the continuous casting and rolling forming is difficult, the formed master batch is processed into phi 1.2, the strength of the welding wire is low, the elongation is low, and the welding requirement cannot be met; in comparative example 2, because Be is not added, the content of Mg can not Be controlled stably, the weld strength and the gold melting strength are low, and the requirement of industrial production can not Be met; comparative example 3 because no B was added, no TiB was present 2 The strength of the welding wire and the strength of the welding seam can not meet the use requirements, and the welding wire and the welding seam can not be used for industrial production; comparative example 4 because Ti refining metal element is excessively added, plasticity of the material is lowered, and plasticity (elongation) of the weld joint is also lowered; the ratio 5 is poor in formability of continuous casting and rolling due to excessive intake of Na, and the performance of the welding line is reduced, so that the service performance of the welding line is reduced; comparative example 6 because of high Si content, mg 2 The strength of the welding wire is improved due to the large amount of Si, but the plasticity is seriously reduced and the requirement of the service performance of the welding wire cannot be met, so that the addition amount of Si cannot be exceeded according to the design concept of the invention0.20wt% of the total weight of the composition; the addition amount of Sr in comparative example 7 is too low, the addition amount of Sr in comparative example 8 is too high, the grains cannot achieve the refining effect due to the too low Sr, the strength of the welding wire is low, and the Sr becomes impurities due to the too high Sr, so that the extensibility of the welding wire and the welding seam is low, and the performance requirements of the welding seam cannot be met; the comparative example 9 does not adopt step annealing, the elongation of the welding wire is only 1%, and the elongation of the welding wire is lower, and the requirement of wire feeding property on the elongation of the welding wire cannot be met. .
Table 3 shows the melting properties of the welding wire of the example of the present invention compared with the comparative welding wire, the brand of which is commonly used in the market ER5356, using a welding base metal 5083.
Table 3 comparison of melting properties of examples and comparative examples
According to the embodiment, the high-performance high-magnesium-manganese-chromium-strontium-aluminum alloy can be obtained, the welding seam strength is higher than that of a common ER5356 welding wire by about 10Mpa, meanwhile, the plasticity of the welding seam is not reduced, a parent rod with the cladding weight of 2 tons can be obtained after continuous casting and rolling, the welding problem and the production efficiency problem caused by adopting an extrusion process are avoided, meanwhile, the parent rod specification is smaller, and compared with the existing continuous casting and rolling process, the manufacturing cost and the equipment cost are lower.
In addition, the tissue schematic of the product prepared by the invention is shown in fig. 1: 1: alpha-Al; 2: mg of 2 Si；3：Al 4 Sr；4：(Fe,Mn,Cr)Al x ；5:Mg 3 Al 2 ；6:TiB 2 The organization schematic diagram shows the distribution condition and the position of each main element in the product organization prepared by the invention.
The various aspects, embodiments, features of the invention are to be considered as illustrative in all respects and not restrictive, the scope of the invention being indicated only by the appended claims. Other embodiments, modifications, and uses will be apparent to those skilled in the art without departing from the spirit and scope of the claimed invention.
In the preparation method of the invention, the sequence of each step is not limited to the listed sequence, and the sequential change of each step is also within the protection scope of the invention without the inventive labor for the person skilled in the art. Furthermore, two or more steps or actions may be performed simultaneously.
Finally, it should be noted that the specific embodiments described herein are merely illustrative of the invention and are not limiting of the invention's embodiments. Those skilled in the art may make various modifications or additions to the described embodiments or substitutions in a similar manner, and need not and cannot fully practice all of the embodiments. While these obvious variations and modifications, which come within the spirit of the invention, are within the scope of the invention, they are to be construed as being without departing from the spirit of the invention.
Claims (7)
1. The preparation method of the high-magnesium-manganese-chromium-strontium-aluminum alloy welding wire is characterized by comprising the following components in percentage by weight:
magnesium: 4.5-5.5wt%; manganese: 0.05-0.20wt%; chromium: 0.05 to 0.09 wt.%; strontium: 0.011-0.05 wt%; titanium: 0.05-0.15 wt%; boron: 0.0002 to 0.05wt%; beryllium: 0.0001 to 0.0005wt%; the balance of aluminum and unavoidable impurity elements; the content of unavoidable impurity elements is less than 0.5wt%; the impurity element includes: less than or equal to 0.020wt% of Pb, less than or equal to 0.015wt% of Sb, less than or equal to 0.015wt% of Bi, less than or equal to 0.015wt% of Te, less than or equal to 0.20wt% of Si, less than or equal to 0.25wt% of Fe, less than or equal to 0.015wt% of Ni, less than or equal to 0.005wt% of Ba, less than or equal to 0.015wt% of Zr, less than or equal to 0.015wt% of Ga, less than or equal to 0.015wt% of P, less than or equal to 0.015wt% of V, less than or equal to 0.005wt% of Ce, less than or equal to 0.0005wt% of Li, less than or equal to 0.0020wt% of Na, and less than or equal to 0.0030wt% of Ca;
the preparation method comprises the following steps: preparing materials according to the components of the high-magnesium-manganese-chromium-strontium-aluminum alloy, smelting, continuously casting and rolling to obtain a master rod, performing plastic processing, annealing, performing plastic processing, peeling and subpackaging on the master rod;
the smelting process adopts a mode of adding rare earth in a smelting furnace for dehydrogenation treatment, and the adding amount of the rare earth is 0.05-0.35% of the mass of the melt;
and after peeling and subpackaging, low-temperature step annealing is performed, wherein the low-temperature step annealing is as follows: the annealing temperature is 50-135 ℃, and the heat preservation is carried out for 3-24 hours at the annealing temperature.
2. The method according to claim 1, wherein Li+Na+Ca is not more than 0.0040wt%.
3. The method according to claim 1, wherein the temperature rise rate at less than 50 ℃ is 25 to 35 ℃/hr and the temperature rise rate at more than 50 ℃ is 5 to 15 ℃/hr during the low-temperature step annealing.
4. A high magnesium manganese chromium strontium aluminum alloy welding wire, characterized in that it is prepared by the preparation method of claim 1.
5. The high-magnesium-manganese-chromium-strontium-aluminum alloy welding wire according to claim 4, wherein the diameter of the high-magnesium-manganese-chromium-strontium-aluminum alloy welding wire is phi 0.8-phi 2.0mm, and the hydrogen content of the high-magnesium-manganese-chromium-strontium-aluminum alloy welding wire is less than 5.30ppm.
6. The high-magnesium-manganese-chromium-strontium-aluminum alloy welding wire according to claim 4, wherein the spring-open diameter of the high-magnesium-manganese-chromium-strontium-aluminum alloy welding wire is phi 350-phi 650mm, and the warpage is less than 20mm.
7. The high-magnesium-manganese-chromium-strontium-aluminum alloy welding wire according to claim 4, wherein the tensile strength of the high-magnesium-manganese-chromium-strontium-aluminum alloy welding wire is 400-480 Mpa, and the welding strength is not lower than 0.63 times of the welding strength.
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Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101824567A (en) * | 2010-05-21 | 2010-09-08 | 桂林市银箭焊接材料有限公司 | Al-Mg alloy welding wire and preparation method thereof |
| CN108588514A (en) * | 2017-12-13 | 2018-09-28 | 新疆众和股份有限公司 | A kind of method of high temperature rolling high-magnesium aluminum alloy bar |
| CN109732239A (en) * | 2019-02-14 | 2019-05-10 | 宁波博德高科股份有限公司 | High magnesium manganese chromium cobalt aluminium alloy and preparation method thereof for manufacturing welding wire |
| CN112930410A (en) * | 2018-11-07 | 2021-06-08 | 日本轻金属株式会社 | Aluminum alloy for die casting and aluminum alloy die casting material |
| CN114193021A (en) * | 2021-11-24 | 2022-03-18 | 宁波博德高科股份有限公司 | Aluminum-silicon-strontium-titanium-boron alloy welding wire and intelligent preparation method thereof |
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Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101824567A (en) * | 2010-05-21 | 2010-09-08 | 桂林市银箭焊接材料有限公司 | Al-Mg alloy welding wire and preparation method thereof |
| CN108588514A (en) * | 2017-12-13 | 2018-09-28 | 新疆众和股份有限公司 | A kind of method of high temperature rolling high-magnesium aluminum alloy bar |
| CN112930410A (en) * | 2018-11-07 | 2021-06-08 | 日本轻金属株式会社 | Aluminum alloy for die casting and aluminum alloy die casting material |
| CN109732239A (en) * | 2019-02-14 | 2019-05-10 | 宁波博德高科股份有限公司 | High magnesium manganese chromium cobalt aluminium alloy and preparation method thereof for manufacturing welding wire |
| CN114193021A (en) * | 2021-11-24 | 2022-03-18 | 宁波博德高科股份有限公司 | Aluminum-silicon-strontium-titanium-boron alloy welding wire and intelligent preparation method thereof |
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