CN119140975A - Magnesium/steel dissimilar metal tube/bar welding interface with multilayer multi-mode characteristics, welding method and application thereof - Google Patents
Magnesium/steel dissimilar metal tube/bar welding interface with multilayer multi-mode characteristics, welding method and application thereof Download PDFInfo
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- 239000011777 magnesium Substances 0.000 title claims abstract description 151
- 239000010959 steel Substances 0.000 title claims abstract description 146
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 145
- 238000003466 welding Methods 0.000 title claims abstract description 141
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 title claims abstract description 135
- 229910052749 magnesium Inorganic materials 0.000 title claims abstract description 135
- 229910052751 metal Inorganic materials 0.000 title claims abstract description 94
- 239000002184 metal Substances 0.000 title claims abstract description 94
- 238000000034 method Methods 0.000 title claims abstract description 47
- 229910017706 MgZn Inorganic materials 0.000 claims abstract description 32
- 210000001503 joint Anatomy 0.000 claims abstract description 21
- 230000007704 transition Effects 0.000 claims abstract description 10
- 239000010953 base metal Substances 0.000 claims description 45
- 239000000463 material Substances 0.000 claims description 33
- 238000000137 annealing Methods 0.000 claims description 22
- 239000002131 composite material Substances 0.000 claims description 21
- 229910009369 Zn Mg Inorganic materials 0.000 claims description 19
- 229910007573 Zn-Mg Inorganic materials 0.000 claims description 19
- 230000008569 process Effects 0.000 claims description 17
- 238000004140 cleaning Methods 0.000 claims description 16
- 229910000851 Alloy steel Inorganic materials 0.000 claims description 8
- 238000005498 polishing Methods 0.000 claims description 8
- 229910000975 Carbon steel Inorganic materials 0.000 claims description 5
- 239000010962 carbon steel Substances 0.000 claims description 5
- 229910003023 Mg-Al Inorganic materials 0.000 claims description 4
- 229910052725 zinc Inorganic materials 0.000 claims description 2
- 239000011701 zinc Substances 0.000 claims 14
- KFZAUHNPPZCSCR-UHFFFAOYSA-N iron zinc Chemical compound [Fe].[Zn] KFZAUHNPPZCSCR-UHFFFAOYSA-N 0.000 claims 1
- 150000001875 compounds Chemical class 0.000 abstract description 15
- 238000004021 metal welding Methods 0.000 abstract description 2
- 239000010410 layer Substances 0.000 description 190
- 239000012071 phase Substances 0.000 description 39
- 230000000052 comparative effect Effects 0.000 description 22
- 239000013078 crystal Substances 0.000 description 16
- 229910000861 Mg alloy Inorganic materials 0.000 description 9
- 150000002739 metals Chemical class 0.000 description 8
- 230000000694 effects Effects 0.000 description 6
- 238000005242 forging Methods 0.000 description 6
- 230000008901 benefit Effects 0.000 description 5
- 238000005516 engineering process Methods 0.000 description 3
- 229910045601 alloy Inorganic materials 0.000 description 2
- 239000000956 alloy Substances 0.000 description 2
- 230000009286 beneficial effect Effects 0.000 description 2
- 230000006870 function Effects 0.000 description 2
- 238000012986 modification Methods 0.000 description 2
- 230000004048 modification Effects 0.000 description 2
- 230000009467 reduction Effects 0.000 description 2
- 239000002356 single layer Substances 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- 229910001209 Low-carbon steel Inorganic materials 0.000 description 1
- 229910000914 Mn alloy Inorganic materials 0.000 description 1
- 229910000691 Re alloy Inorganic materials 0.000 description 1
- 229910001297 Zn alloy Inorganic materials 0.000 description 1
- 229910001093 Zr alloy Inorganic materials 0.000 description 1
- 238000010521 absorption reaction Methods 0.000 description 1
- 230000006978 adaptation Effects 0.000 description 1
- 238000012512 characterization method Methods 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 230000009977 dual effect Effects 0.000 description 1
- 239000003344 environmental pollutant Substances 0.000 description 1
- 230000004927 fusion Effects 0.000 description 1
- 238000011065 in-situ storage Methods 0.000 description 1
- 230000000977 initiatory effect Effects 0.000 description 1
- 239000011229 interlayer Substances 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
- 238000005304 joining Methods 0.000 description 1
- 239000007791 liquid phase Substances 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 238000010297 mechanical methods and process Methods 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 231100000719 pollutant Toxicity 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 230000035939 shock Effects 0.000 description 1
- 239000007790 solid phase Substances 0.000 description 1
- 238000003756 stirring Methods 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
Classifications
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K20/00—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating
- B23K20/10—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating making use of vibrations, e.g. ultrasonic welding
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K20/00—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating
- B23K20/24—Preliminary treatment
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K2103/00—Materials to be soldered, welded or cut
- B23K2103/18—Dissimilar materials
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- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Pressure Welding/Diffusion-Bonding (AREA)
Abstract
The invention discloses a magnesium/steel dissimilar metal tube/bar welding interface with multilayer multi-mode characteristics, and a welding method and application thereof, and belongs to the technical field of magnesium/steel dissimilar metal welding. The welding interface of the magnesium/steel dissimilar metal tube/bar with the multi-layer multi-mode characteristic comprises three layers, namely a Mg-Zn layer, a Zn layer and a Fe-Zn layer, wherein the average grain size of the Mg-Zn layer is smaller than 2 mu m and contains MgZn precipitated phases, the size of the precipitated phases is smaller than 100nm, the average grain size of the Zn layer is smaller than 2 mu m, the Fe-Zn layer contains an Fe-Zn compound transition phase, and the thicknesses of the Mg-Zn layer, the Zn layer and the Fe-Zn layer are respectively 10-40 mu m, 1-4 mu m and 4-16 mu m. The invention can butt joint the magnesium/steel dissimilar metal pipes/bars, and expands the application range of ultrasonic welding to the shape and welding mode of the magnesium/steel dissimilar metal.
Description
Technical Field
The invention relates to a magnesium/steel dissimilar metal tube/bar welding interface with multilayer multi-mode characteristics, and a welding method and application thereof, belonging to the technical field of magnesium/steel dissimilar metal welding.
Background
The magnesium alloy has the advantages of high specific strength, high specific rigidity, excellent electromagnetic shielding capability, good thermal conductivity, good shock absorption, rich resource reserves, low density and the like, and has good development prospect in the fields of aerospace, automobiles, electronic products and the like. While steel has a high absolute strength, it is still not an alternative on the important load bearing structure of the car body. Due to the application intersection of steel and magnesium alloy, the composite structure of the steel and the magnesium alloy can replace a steel structure in some occasions, so that the weight of the structural member is reduced. Therefore, the connection of the magnesium alloy and the steel dissimilar metal has wide application prospect. At present, the connection of magnesium alloy and steel is mainly realized by mechanical methods such as bolts, riveting and the like, the production efficiency is low, the cost is high, and the joint has additional weight, so that the technology of welding the dissimilar metals of the magnesium/steel with high efficiency, low cost, light weight and high comprehensive cost performance is necessary to develop. However, because the magnesium alloy and the steel have large difference in physical and chemical properties, the liquid phases of the magnesium alloy and the steel can not coexist, metallurgical bonding can hardly be formed, direct fusion welding of the magnesium alloy and the steel is very difficult, and effective connection can not be formed.
The ultrasonic welding is a typical solid-phase welding technology which does not cause melting of materials, has the characteristics of short welding time, simple operation, stable process, good forming, relative insensitivity to surface oxides and pollutants and the like, and is a connecting method which has potential advantages and is suitable for magnesium alloy/steel dissimilar metals. And, based on the difficult problem that the metallurgical bonding is difficult to form caused by the difference of the physical and chemical properties of the dissimilar metals of magnesium/steel, adding an intermediate layer is a good solution. However, the welding effect of the current ultrasonic welding products for metals needs to be further improved, the welding effect is limited to only lap joint of plates, the application range is greatly limited, and the added intermediate layer is single, and a Zn layer is usually added. A single metal interlayer tends to produce a continuous hard brittle Mg-Zn phase, resulting in reduced mechanical properties.
Therefore, based on the problems, the invention prepares the magnesium/steel dissimilar metal pipe/bar weldment with a multi-layer multi-mode characteristic welding interface by utilizing the rotary ultrasonic welding process, improves the connection strength of the magnesium/steel dissimilar metal ultrasonic welding weldment, and realizes the butt joint of the magnesium/steel dissimilar metal pipe/bar.
Disclosure of Invention
Aiming at the problems that the existing ultrasonic welding effect is poor, the shape and the connecting mode of the applicable material are limited, and a magnesium/steel dissimilar metal ultrasonic welding connecting interface caused by a single intermediate layer is easy to generate a hard and brittle intermetallic compound, so that the strength of the connecting interface is low, the invention aims to provide a method for obtaining a magnesium/steel dissimilar metal pipe/bar weldment with a multi-layer multi-mode characteristic welding interface by utilizing rotary ultrasonic welding.
Meanwhile, the invention provides a magnesium/steel dissimilar metal tube/bar welding interface with multi-layer and multi-mode characteristics.
Meanwhile, the invention provides a magnesium/steel dissimilar metal tube/bar weldment obtained by adopting the welding method of the magnesium/steel dissimilar metal tube/bar welding interface with multi-layer multi-mode characteristics.
Meanwhile, the invention provides application of the magnesium/steel dissimilar metal tube/bar weldment in automobile industrial workpieces (such as car door frames, engine brackets and the like), aerospace workpieces (such as seat frames, aircraft wings, landing gear and the like) and electronic products (such as notebook computer shells and supports, mobile phone middle frames and the like).
In order to solve the technical problems, the invention adopts the following technical scheme:
the welding interface of the magnesium/steel dissimilar metal tube/bar with the multi-layer multi-mode characteristic comprises three layers, namely a Mg-Zn layer, a Zn layer and a Fe-Zn layer, wherein the average grain size of the Mg-Zn layer is smaller than 2 mu m, the MgZn precipitated phase is contained, the size of the precipitated phase is smaller than 100nm, the average grain size of the Zn layer is smaller than 2 mu m, the Fe-Zn layer contains an Fe-Zn compound transition phase, and the thicknesses of the Mg-Zn layer, the Zn layer and the Fe-Zn layer are respectively 10-40 mu m, 1-4 mu m and 4-16 mu m.
A method of welding a magnesium/steel dissimilar metal tube/bar weld interface having a multi-layer multi-modal characteristic, comprising the steps of:
S1, cleaning a base metal, namely polishing and cleaning the section of a welded magnesium, steel base metal pipe or rod;
S2, preparing an intermediate layer, namely forming a Zn-Mg composite intermediate layer by pure Zn and pure Mg according to the arrangement sequence of Zn/Mg/Zn;
s3, fixing a welded component, namely placing the cleaned parent metal and a Zn-Mg composite intermediate layer on a workbench of a rotary ultrasonic welder, forming a butt joint structure under magnesium upper steel, and placing the Zn-Mg composite intermediate layer in the center of a parent metal butt joint region;
S4, welding, namely performing rotary ultrasonic welding on the fixed welded component, wherein ultrasonic parameters are that the output frequency is 20kHz, the working power is 1000-5000W, the amplitude is 10-50 mu m, and the whole process is divided into three stages, namely, the first stage is 0.5-2S, and the rotating speed is 500-1000 r/min; the second stage is 2-4S, the rotating speed is 1000-2000 r/min, the third stage is 4-5S, and the rotating speed is 100-500 r/min, so as to obtain a pipe/bar butt welding piece;
and S5, short-time annealing, namely annealing the obtained pipe/bar butt welding piece to obtain the magnesium/steel dissimilar metal pipe/bar welding interface with multi-layer multi-mode characteristics.
Preferably, the magnesium is selected from any one of the series Mg-Al, mg-Zn, mg-Mn, mg-Zr and Mg-RE, and the steel is selected from any one of carbon steel, alloy steel and high alloy steel.
Preferably, in S1, the magnesium and the steel are both tubular or rod-shaped, the inner diameter of the pipe is 4.5 mm-28 mm, the outer diameter is 6 mm-30 mm, the length is 10-40 mm, the difference between the inner diameter and the outer diameter is 1.5-5 mm, the diameter of the bar is 3-15 mm, the length is 10-40 mm, and the inner diameter and the outer diameter or the diameter of the magnesium material and the steel material are the same.
Preferably, in S2, the inner and outer diameters of the Zn-Mg composite intermediate layer are the same as those of magnesium and steel.
Preferably, in S4, the triggering condition of the rotary ultrasonic welding is that the pressure head reaches 0.4MPa for the base metal to be welded.
Preferably, in S5, the annealing temperature is 150-220 ℃ and the annealing time is 20 min-1 h.
The tensile strength of the magnesium/steel dissimilar metal pipe/bar weldment obtained by adopting the welding method reaches more than 120 MPa.
The magnesium/steel dissimilar metal tube/bar weldment of the invention is applied to automobile industry workpieces, aerospace workpieces and electronic products.
The automobile industry workpiece comprises a vehicle door frame and an engine bracket, the aerospace workpiece comprises a seat frame, an aircraft wing and a landing gear, and the electronic product comprises a notebook computer shell, a bracket and a mobile phone middle frame.
The invention adopts a rotary ultrasonic welding process and an obtained multi-layer multi-mode characteristic welding interface to improve the quality of welding seams, and the specific principle is that (1) the rotary ultrasonic welding process adds a rotary function on a tool head on the basis of traditional ultrasonic welding, the rotation of the tool head is beneficial to the generation of more friction heat of welded materials so as to fully soften the welded materials, and meanwhile, the rotating tool head also provides a certain stirring effect so as to fully contact the softened parts of two welded parts, thereby achieving the aim of effective combination and further providing the welding quality of joints. (2) The multi-layer multi-mode interface obtained after rotary ultrasonic welding is a multi-layer multi-mode interface of 'parent metal magnesium/MgZn layer (superfine crystal+nano MgZn precipitated phase)/Zn layer (superfine crystal)/Fe-Zn layer (containing Fe-Zn compound)/parent metal steel', compared with the traditional welding, the multi-layer multi-mode interface has the advantages that the interface transition is good, and the problem of strength reduction caused by single-layer Mg-Zn interface brittleness is reduced. Meanwhile, the MgZn layer and the Zn layer are provided with ultrafine crystal grains, and the MgZn precipitated phase is a nano precipitated phase, so that better strengthening effect is achieved on the interface, crack initiation and expansion can be effectively prevented, and the interface connection strength of the magnesium/steel dissimilar metal is remarkably improved.
Compared with the prior art, the invention has the beneficial effects that:
(1) The strength of the obtained multi-layer multi-mode characteristic magnesium/steel dissimilar metal tube/bar welding interface is obviously improved, the tensile strength can reach more than 120MPa, and the strength is higher than that of the magnesium/steel dissimilar metal plate lap joint weldment interface obtained by ultrasonic welding adopted at present.
(2) The multi-layer multi-mode characteristic magnesium/steel dissimilar metal tube/bar welding interface obtained by the invention is a multi-layer (the welding interface obtained from the magnesium side to the steel side comprises three layers, namely a Mg-Zn layer, a Zn layer and a Fe-Zn layer, wherein the average grain size of the Mg-Zn layer is smaller than 2 mu m, and the MgZn precipitated phase is contained, the size of the precipitated phase is smaller than 100nm, and the average grain size of the Zn layer is smaller than 2 mu m), the multi-layer interface overcomes the problem of strength reduction caused by brittleness of a single-layer Mg-Zn interface, and the MgZn layer and the Zn layer with superfine crystals and the nano MgZn precipitated phase further strengthen the interface, thereby improving the connection strength of the magnesium/steel dissimilar metal interface.
(3) The rotary ultrasonic welding mode has the advantages of simple processing mode, high efficiency, small heat input, no pollution and low cost, and the obtained product has better welding effect compared with the common ultrasonic welding mode due to the rotary function introduced into the tool head, thereby having wide application prospect.
(4) The rotary ultrasonic welding mode can be used for butt joint of the magnesium/steel dissimilar metal pipes/bars, breaks through the limitation that the ultrasonic welding is only used for lap joint of plates when the magnesium/steel dissimilar metals are welded at present, and expands the application range of the ultrasonic welding to the shapes and the welding modes of the magnesium/steel dissimilar metals.
Drawings
FIG. 1 is a microstructure of a Mg-Zn layer of the invention after spin ultrasonic welding;
FIG. 2 is a microstructure of MgZn precipitated phases in the Mg-Zn layer after spin ultrasonic welding according to the present invention.
Detailed Description
The invention will now be described in further detail with reference to the drawings and to specific examples. The following examples are only illustrative of the present invention and are not intended to limit the scope of the invention.
Example 1
A welding interface of a magnesium/steel dissimilar metal pipe with a multi-layer multi-mode characteristic comprises three layers, namely a Mg-Zn layer, a Zn layer and a Fe-Zn layer, wherein the average grain size of the Mg-Zn layer is smaller than 2 mu m, the MgZn precipitated phase is contained, the size of the precipitated phase is smaller than 100nm, and the average grain size of the Zn layer is smaller than 2 mu m.
The thicknesses of the Mg-Zn layer, the Zn layer and the Fe-Zn layer were 20 μm, 2 μm and 10 μm, respectively.
The Fe-Zn layer contains Fe-Zn compound transition phase.
The section of the welding forging piece of the magnesium/steel dissimilar metal pipe has the following structure of a base metal magnesium/MgZn layer (superfine crystal+nanometer MgZn precipitated phase)/Zn layer (superfine crystal)/Fe-Zn layer (containing Fe-Zn compound)/base metal steel.
A method for welding magnesium/steel dissimilar metal tubing capable of forming a multi-layer multi-mode characteristic welding interface comprises the following steps:
S1, cleaning a base metal, namely polishing and cleaning the section of a welded magnesium and steel base metal pipe, wherein the magnesium material is Mg-Al alloy, the steel material is carbon steel, the base metal magnesium and the steel are both tubular, the inner diameter of the pipe is 15mm, the outer diameter of the pipe is 20mm, the length of the pipe is 20mm, the difference between the inner diameter and the outer diameter is 5mm, and the inner diameter and the outer diameter of the magnesium material and the steel material are the same;
S2, preparing a middle layer, namely forming a Zn-Mg composite middle layer by pure Zn and pure Mg according to the arrangement sequence of Zn/Mg/Zn, wherein the inner and outer diameters of the Zn-Mg composite middle layer are the same as those of a magnesium and steel parent metal;
s3, fixing a welded component, namely placing the cleaned parent metal and an intermediate layer on a workbench of a rotary ultrasonic welder, forming a butt joint structure of magnesium upper steel and magnesium lower steel, and placing the intermediate layer in the center of a butt joint region of the parent metal;
s4, welding, namely performing rotary ultrasonic welding on the fixed welded component, wherein ultrasonic parameters are that the output frequency is 20kHz, the working power is 2500W, the amplitude is 30 mu m, and the whole process is divided into three stages, namely, the first stage is 0.5-2S, the rotating speed is 800r/min, the second stage is 2-4S, the rotating speed is 1500r/min, the third stage is 4-5S, the rotating speed is 300r/min, and the triggering condition of the rotary ultrasonic welding is that the pressure of a pressure head on a base metal to be welded reaches 0.4MPa;
and S5, short-time annealing, namely annealing the obtained pipe butt welding piece at the annealing temperature of 200 ℃ for 30min to obtain the welding interface of the magnesium/steel dissimilar metal pipe with the multi-layer multi-mode characteristic.
The magnesium/steel dissimilar metal pipe weldment obtained by adopting the welding method in the embodiment is applied to automobile industrial workpieces, aerospace workpieces and electronic products.
The automobile industry workpiece comprises a vehicle door frame and an engine bracket, the aerospace workpiece comprises a seat frame, an aircraft wing and a landing gear, and the electronic product comprises a notebook computer shell, a bracket and a mobile phone middle frame.
As shown in FIG. 1, the graph is a microstructure graph of the Mg-Zn layer, wherein the maximum grain size is smaller than 2 mu m, and the requirement that the average grain size of the Mg-Zn layer is smaller than 2 mu m is met;
as shown in FIG. 2, the graph is a microstructure graph of MgZn precipitated phases in the Mg-Zn layer, wherein dark dots are MgZn precipitated phases, the maximum size is smaller than 80nm, and the requirement that the size of the MgZn precipitated phases is smaller than 100nm is met.
Example 2
A welding interface of a magnesium/steel dissimilar metal pipe with a multi-layer multi-mode characteristic comprises three layers, namely a Mg-Zn layer, a Zn layer and a Fe-Zn layer, wherein the average grain size of the Mg-Zn layer is smaller than 2 mu m, the MgZn precipitated phase is contained, the size of the precipitated phase is smaller than 100nm, and the average grain size of the Zn layer is smaller than 2 mu m.
The thicknesses of the Mg-Zn layer, the Zn layer and the Fe-Zn layer were 10 μm, 1 μm and 4 μm, respectively.
The Fe-Zn layer contains Fe-Zn compound transition phase.
The section of the welding forging piece of the magnesium/steel dissimilar metal pipe has the following structure of a base metal magnesium/MgZn layer (superfine crystal+nanometer MgZn precipitated phase)/Zn layer (superfine crystal)/Fe-Zn layer (containing Fe-Zn compound)/base metal steel.
A method for welding magnesium/steel dissimilar metal tubing capable of forming a multi-layer multi-mode characteristic welding interface comprises the following steps:
S1, cleaning a base metal, namely polishing and cleaning the section of a welded magnesium and steel base metal pipe, wherein the magnesium material is Mg-Zn alloy, the steel material is alloy steel, the base metal magnesium and the steel are both tubular, the inner diameter of the pipe is 4.5mm, the outer diameter of the pipe is 6mm, the length of the pipe is 10mm, the difference between the inner diameter and the outer diameter is 1.5mm, and the inner diameter and the outer diameter of the magnesium material and the steel material are the same;
S2, preparing a middle layer, namely forming a Zn-Mg composite middle layer by pure Zn and pure Mg according to the arrangement sequence of Zn/Mg/Zn, wherein the inner and outer diameters of the Zn-Mg composite middle layer are the same as those of a magnesium and steel parent metal;
s3, fixing a welded component, namely placing the cleaned parent metal and an intermediate layer on a workbench of a rotary ultrasonic welder, forming a butt joint structure of magnesium upper steel and magnesium lower steel, and placing the intermediate layer in the center of a butt joint region of the parent metal;
S4, welding, namely performing rotary ultrasonic welding on the fixed welded component, wherein ultrasonic parameters are that the output frequency is 20kHz, the working power is 1000W, the amplitude is 10 mu m, and the whole process is divided into three stages, namely, the first stage is 0.5-2S, the rotating speed is 500r/min, the second stage is 2-4S, the rotating speed is 1000r/min, the third stage is 4-5S, the rotating speed is 100r/min, and the triggering condition of the rotary ultrasonic welding is that the pressure of a pressure head on a base metal to be welded reaches 0.4MPa;
And S5, short-time annealing, namely annealing the obtained pipe butt welding piece at the annealing temperature of 150 ℃ for 20min to obtain the welding interface of the magnesium/steel dissimilar metal pipe with the multi-layer multi-mode characteristic.
The magnesium/steel dissimilar metal pipe weldment obtained by adopting the welding method in the embodiment is applied to automobile industrial workpieces, aerospace workpieces and electronic products.
The automobile industry workpiece comprises a vehicle door frame and an engine bracket, the aerospace workpiece comprises a seat frame, an aircraft wing and a landing gear, and the electronic product comprises a notebook computer shell, a bracket and a mobile phone middle frame.
Example 3
A welding interface of a magnesium/steel dissimilar metal pipe with a multi-layer multi-mode characteristic comprises three layers, namely a Mg-Zn layer, a Zn layer and a Fe-Zn layer, wherein the average grain size of the Mg-Zn layer is smaller than 2 mu m, the MgZn precipitated phase is contained, the size of the precipitated phase is smaller than 100nm, and the average grain size of the Zn layer is smaller than 2 mu m.
The thicknesses of the Mg-Zn layer, the Zn layer and the Fe-Zn layer were 40 μm, 4 μm and 16 μm, respectively.
The Fe-Zn layer contains Fe-Zn compound transition phase.
The section of the welding forging piece of the magnesium/steel dissimilar metal pipe has the following structure of a base metal magnesium/MgZn layer (superfine crystal+nanometer MgZn precipitated phase)/Zn layer (superfine crystal)/Fe-Zn layer (containing Fe-Zn compound)/base metal steel.
A method for welding magnesium/steel dissimilar metal tubing capable of forming a multi-layer multi-mode characteristic welding interface comprises the following steps:
S1, cleaning a base metal, namely polishing and cleaning the section of a welded magnesium and steel base metal pipe, wherein the magnesium material is Mg-Mn alloy, the steel material is high alloy steel, the base metal magnesium and the steel are both tubular, the inner diameter of the pipe is 28mm, the outer diameter of the pipe is 30mm, the length of the pipe is 40mm, the difference between the inner diameter and the outer diameter is 2mm, and the inner diameter and the outer diameter of the magnesium material and the steel material are the same;
S2, preparing a middle layer, namely forming a Zn-Mg composite middle layer by pure Zn and pure Mg according to the arrangement sequence of Zn/Mg/Zn, wherein the inner and outer diameters of the Zn-Mg composite middle layer are the same as those of a magnesium and steel parent metal;
s3, fixing a welded component, namely placing the cleaned parent metal and an intermediate layer on a workbench of a rotary ultrasonic welder, forming a butt joint structure of magnesium upper steel and magnesium lower steel, and placing the intermediate layer in the center of a butt joint region of the parent metal;
S4, welding, namely performing rotary ultrasonic welding on the fixed welded component, wherein ultrasonic parameters are that the output frequency is 20kHz, the working power is 5000W, the amplitude is 50 mu m, the whole process is divided into three stages, namely, the first stage is 0.5-2S, the rotating speed is 1000r/min, the second stage is 2-4S, the rotating speed is 2000r/min, the third stage is 4-5S, the rotating speed is 500r/min, and the triggering condition of the rotary ultrasonic welding is that the pressure of a pressure head on a base metal to be welded reaches 0.4MPa;
and S5, short-time annealing, namely annealing the obtained pipe butt welding piece at 220 ℃ for 1 hour to obtain a welding interface of the magnesium/steel dissimilar metal pipe with multi-layer and multi-mode characteristics.
The magnesium/steel dissimilar metal pipe weldment obtained by adopting the welding method in the embodiment is applied to automobile industrial workpieces, aerospace workpieces and electronic products.
The automobile industry workpiece comprises a vehicle door frame and an engine bracket, the aerospace workpiece comprises a seat frame, an aircraft wing and a landing gear, and the electronic product comprises a notebook computer shell, a bracket and a mobile phone middle frame.
Example 4
A welding interface of a magnesium/steel dissimilar metal bar with a multi-layer multi-mode characteristic comprises three layers, namely a Mg-Zn layer, a Zn layer and a Fe-Zn layer, wherein the average grain size of the Mg-Zn layer is smaller than 2 mu m, the MgZn precipitated phase is contained, the size of the precipitated phase is smaller than 100nm, and the average grain size of the Zn layer is smaller than 2 mu m.
The thicknesses of the Mg-Zn layer, the Zn layer and the Fe-Zn layer are 15 μm, 2 μm and 15 μm respectively.
The Fe-Zn layer contains Fe-Zn compound transition phase.
The section of the magnesium/steel dissimilar metal bar welding forging has the following structure of a base metal magnesium/MgZn layer (superfine crystal+nanometer MgZn precipitated phase)/Zn layer (superfine crystal)/Fe-Zn layer (containing Fe-Zn compound)/base metal steel.
A method for welding dissimilar metal magnesium/steel bars capable of forming a multi-layer multi-mode characteristic welding interface comprises the following steps:
S1, cleaning a base metal, namely polishing and cleaning the section of a welded magnesium and steel base metal rod, wherein the magnesium material is Mg-Zr alloy, the steel material is high alloy steel, the base metal magnesium and the steel are both rod-shaped, the diameter of the rod is 10mm, the length of the rod is 20mm, and the diameters of the magnesium material and the steel material are the same;
S2, preparing an intermediate layer, namely forming a Zn-Mg composite intermediate layer by pure Zn and pure Mg according to the arrangement sequence of Zn/Mg/Zn, wherein the diameter of the Zn-Mg composite intermediate layer is the same as that of a magnesium and steel base metal;
s3, fixing a welded component, namely placing the cleaned parent metal and an intermediate layer on a workbench of a rotary ultrasonic welder, forming a butt joint structure of magnesium upper steel and magnesium lower steel, and placing the intermediate layer in the center of a butt joint region of the parent metal;
S4, welding, namely performing rotary ultrasonic welding on the fixed welded component, wherein ultrasonic parameters are that the output frequency is 20kHz, the working power is 5000W, the amplitude is 50 mu m, the whole process is divided into three stages, namely, the first stage is 0.5-2S, the rotating speed is 1000r/min, the second stage is 2-4S, the rotating speed is 2000r/min, the third stage is 4-5S, the rotating speed is 500r/min, and the triggering condition of the rotary ultrasonic welding is that the pressure of a pressure head on a base metal to be welded reaches 0.4MPa;
and S5, short-time annealing, namely annealing the obtained bar butt-welded piece at 220 ℃ for 1h to obtain the magnesium/steel dissimilar metal bar welding interface with multi-layer and multi-mode characteristics.
The magnesium/steel dissimilar metal bar weldment obtained by adopting the welding method in the embodiment is applied to automobile industrial workpieces, aerospace workpieces and electronic products.
The automobile industry workpiece comprises a vehicle door frame and an engine bracket, the aerospace workpiece comprises a seat frame, an aircraft wing and a landing gear, and the electronic product comprises a notebook computer shell, a bracket and a mobile phone middle frame.
Example 5
A welding interface of a magnesium/steel dissimilar metal bar with a multi-layer multi-mode characteristic comprises three layers, namely a Mg-Zn layer, a Zn layer and a Fe-Zn layer, wherein the average grain size of the Mg-Zn layer is smaller than 2 mu m, the MgZn precipitated phase is contained, the size of the precipitated phase is smaller than 100nm, and the average grain size of the Zn layer is smaller than 2 mu m.
The thicknesses of the Mg-Zn layer, the Zn layer and the Fe-Zn layer were 10 μm, 1 μm and 4 μm, respectively.
The Fe-Zn layer contains Fe-Zn compound transition phase.
The section of the magnesium/steel dissimilar metal bar welding forging has the following structure of a base metal magnesium/MgZn layer (superfine crystal+nanometer MgZn precipitated phase)/Zn layer (superfine crystal)/Fe-Zn layer (containing Fe-Zn compound)/base metal steel.
A method for welding dissimilar metal magnesium/steel bars capable of forming a multi-layer multi-mode characteristic welding interface comprises the following steps:
S1, cleaning a base metal, namely polishing and cleaning the section of a welded magnesium and steel base metal rod, wherein the magnesium material is Mg-RE alloy, the steel material is carbon steel, the base metal magnesium and the steel are both rod-shaped, the diameter of the rod is 3mm, the length of the rod is 10mm, and the diameters of the magnesium material and the steel material are the same;
S2, preparing an intermediate layer, namely forming a Zn-Mg composite intermediate layer by pure Zn and pure Mg according to the arrangement sequence of Zn/Mg/Zn, wherein the diameter of the Zn-Mg composite intermediate layer is the same as that of a magnesium and steel base metal;
s3, fixing a welded component, namely placing the cleaned parent metal and an intermediate layer on a workbench of a rotary ultrasonic welder, forming a butt joint structure of magnesium upper steel and magnesium lower steel, and placing the intermediate layer in the center of a butt joint region of the parent metal;
S4, welding, namely performing rotary ultrasonic welding on the fixed welded component, wherein ultrasonic parameters are that the output frequency is 20kHz, the working power is 1000W, the amplitude is 10 mu m, and the whole process is divided into three stages, namely, the first stage is 0.5-2S, the rotating speed is 500r/min, the second stage is 2-4S, the rotating speed is 1000r/min, the third stage is 4-5S, the rotating speed is 100r/min, and the triggering condition of the rotary ultrasonic welding is that the pressure of a pressure head on a base metal to be welded reaches 0.4MPa;
And S5, short-time annealing, namely annealing the obtained bar butt-welded piece at the annealing temperature of 150 ℃ for 20min to obtain the magnesium/steel dissimilar metal bar welding interface with multi-layer and multi-mode characteristics.
The magnesium/steel dissimilar metal bar weldment obtained by adopting the welding method in the embodiment is applied to automobile industrial workpieces, aerospace workpieces and electronic products.
The automobile industry workpiece comprises a vehicle door frame and an engine bracket, the aerospace workpiece comprises a seat frame, an aircraft wing and a landing gear, and the electronic product comprises a notebook computer shell, a bracket and a mobile phone middle frame.
Example 6
A welding interface of a magnesium/steel dissimilar metal bar with a multi-layer multi-mode characteristic comprises three layers, namely a Mg-Zn layer, a Zn layer and a Fe-Zn layer, wherein the average grain size of the Mg-Zn layer is smaller than 2 mu m, the MgZn precipitated phase is contained, the size of the precipitated phase is smaller than 100nm, and the average grain size of the Zn layer is smaller than 2 mu m.
The thicknesses of the Mg-Zn layer, the Zn layer and the Fe-Zn layer were 40 μm, 4 μm and 16 μm, respectively.
The Fe-Zn layer contains Fe-Zn compound transition phase.
The section of the magnesium/steel dissimilar metal bar welding forging has the following structure of a base metal magnesium/MgZn layer (superfine crystal+nanometer MgZn precipitated phase)/Zn layer (superfine crystal)/Fe-Zn layer (containing Fe-Zn compound)/base metal steel.
A method for welding dissimilar metal magnesium/steel bars capable of forming a multi-layer multi-mode characteristic welding interface comprises the following steps:
s1, cleaning a base metal, namely polishing and cleaning the section of a welded magnesium and steel base metal rod, wherein the magnesium material is Mg-Al alloy, the steel material is carbon steel, the base metal magnesium and the steel are both rod-shaped, the diameter of the rod is 15mm, the length of the rod is 40mm, and the diameters of the magnesium material and the steel material are the same;
S2, preparing an intermediate layer, namely forming a Zn-Mg composite intermediate layer by pure Zn and pure Mg according to the arrangement sequence of Zn/Mg/Zn, wherein the diameter of the Zn-Mg composite intermediate layer is the same as that of a magnesium and steel base metal;
s3, fixing a welded component, namely placing the cleaned parent metal and an intermediate layer on a workbench of a rotary ultrasonic welder, forming a butt joint structure of magnesium upper steel and magnesium lower steel, and placing the intermediate layer in the center of a butt joint region of the parent metal;
S4, welding, namely performing rotary ultrasonic welding on the fixed welded component, wherein ultrasonic parameters are that the output frequency is 20kHz, the working power is 2000W, the amplitude is 20 mu m, the whole process is divided into three stages, namely, the first stage is 0.5-2S, the rotating speed is 600r/min, the second stage is 2-4S, the rotating speed is 1800r/min, the third stage is 4-5S, the rotating speed is 400r/min, and the triggering condition of the rotary ultrasonic welding is that the pressure of a pressure head on a base metal to be welded reaches 0.4MPa;
And S5, short-time annealing, namely annealing the obtained bar butt-welded piece at 180 ℃ for 40min to obtain the magnesium/steel dissimilar metal bar welding interface with multi-layer and multi-mode characteristics.
The magnesium/steel dissimilar metal bar weldment obtained by adopting the welding method in the embodiment is applied to automobile industrial workpieces, aerospace workpieces and electronic products.
The automobile industry workpiece comprises a vehicle door frame and an engine bracket, the aerospace workpiece comprises a seat frame, an aircraft wing and a landing gear, and the electronic product comprises a notebook computer shell, a bracket and a mobile phone middle frame.
Comparative example 1
The comparative example describes the tensile strength of ultrasonic welding of magnesium/steel dissimilar materials as known in the prior art, and is specifically shown in table 1 below.
TABLE 1 tensile Strength of ultrasonic welding of magnesium/Steel dissimilar materials currently available
Test standard of tube/bar welding tensile test method is GB/T2651-2008/ISO 4136:2001.
【1】 Meng Yu ultrasonic welding of dissimilar metals of magnesium/steel joint structure and mechanical properties [ D ]. University of Jilin, 2024.
【2】Chen J,Lim Y C,Leonard D,et al.In Situ and Post-Mortem Characterizations of Ultrasonic Spot Welded AZ31B and Coated Dual Phase 590Steel Joints[J].Metals(Basel).2020,10(7):899.
【3】Rinker T J,Pan J,Santella M,et al.Fatigue behavior of dissimilar ultrasonic welds in lap-shear specimens of AZ31 and steel sheets[J].Engineering Fracture Mechanics,2018,189(C):405-426.
【4】Santella M,Brown E,Pozuelo M,et al.Details of Mg-Zn reactions in AZ31 to galvanised mild steel ultrasonic spot welds[J].Science and Technology of Welding and Joining,2012,17(3):219-224.
Comparative example 2
The comparative example differs from example 1 only in that the thicknesses of the Mg-Zn layer, fe-Zn layer were 5 μm, 2 μm, 10 μm, respectively.
Comparative example 3
The comparative example differs from example 1 only in that the thicknesses of the Mg-Zn layer, fe-Zn layer were 45 μm, 2 μm, 10 μm, respectively.
Comparative example 4
The comparative example differs from example 1 only in that the thicknesses of the Mg-Zn layer, fe-Zn layer were 20 μm, 5 μm, 10 μm, respectively.
Comparative example 5
The comparative example differs from example 1 only in that the thicknesses of the Mg-Zn layer, fe-Zn layer were 20 μm, 0.5 μm, 10 μm, respectively.
Comparative example 6
The comparative example differs from example 1 only in that the thicknesses of the Mg-Zn layer, fe-Zn layer were 20 μm, 2 μm, and 2 μm, respectively.
Comparative example 7
The comparative example differs from example 1 only in that the thicknesses of the Mg-Zn layer, fe-Zn layer were 20 μm, 2 μm, and 20 μm, respectively.
Comparative example 8
The comparative example differs from example 1 only in that the whole process of the rotary ultrasonic welding is one stage, namely 0.5-5 s, and the rotating speed is 1000r/min.
Comparative example 9
The comparative example differs from example 1 only in that the whole process of the rotary ultrasonic welding is two stages, namely, the first stage is 0.5-2 s, the rotating speed is 800r/min, the second stage is 2-5 s, and the rotating speed is 1000r/min.
Comparative example 10
The comparison example is different from the example 1 only in that the whole process of the rotary ultrasonic welding is four stages, namely, the first stage is 0.5-2 s, the rotating speed is 800r/min, the second stage is 2-4 s, the rotating speed is 1500r/min, the third stage is 4-5 s, the rotating speed is 300r/min, the fourth stage is 5-6 s, and the rotating speed is 500r/min.
Comparative example 11
The comparison example is different from the example 1 only in that the whole process of the rotary ultrasonic welding is three stages, namely, the first stage is 0.5-2 s, the rotating speed is 400r/min, the second stage is 2-4 s, the rotating speed is 1500r/min, the third stage is 4-5 s, and the rotating speed is 300r/min.
Comparative example 12
The comparison example is different from the example 1 only in that the whole process of the rotary ultrasonic welding is three stages, namely, the first stage is 0.5-2 s, the rotating speed is 1200r/min, the second stage is 2-4 s, the rotating speed is 1500r/min, the third stage is 4-5 s, and the rotating speed is 300r/min.
Tensile strength data of the magnesium/steel dissimilar metal tube/bar weldments obtained in examples 1 to 6 and comparative examples 2 to 12 of the present invention are shown in table 2 below.
Table 2 tensile strength data
It should be appreciated that in the above description of exemplary embodiments of the invention, various features of the invention are sometimes grouped together in a single embodiment, figure, or description thereof for the purpose of streamlining the disclosure and aiding in the understanding of one or more of the various inventive aspects. This method of disclosure, however, is not to be interpreted as reflecting an intention that the claimed invention requires more features than are expressly recited in each claim. Rather, as the following claims reflect, inventive aspects lie in less than all features of a single foregoing disclosed embodiment. Thus, the claims following the detailed description are hereby expressly incorporated into this detailed description, with each claim standing on its own as a separate embodiment of this invention.
While the invention has been described with respect to a limited number of embodiments, those skilled in the art, having benefit of the above description, will appreciate that other embodiments are contemplated within the scope of the invention as described herein. Furthermore, it should be noted that the language used in the specification has been principally selected for readability and instructional purposes, and may not have been selected to delineate or circumscribe the inventive subject matter. Accordingly, many modifications and variations will be apparent to those of ordinary skill in the art without departing from the scope and spirit of the appended claims. The disclosure of the present invention is intended to be illustrative, but not limiting, of the scope of the invention, which is defined by the appended claims.
The foregoing is merely a preferred embodiment of the present invention and it should be noted that modifications and adaptations to those skilled in the art may be made without departing from the principles of the present invention, which are intended to be comprehended within the scope of the present invention.
Claims (10)
1. A welding interface of a magnesium/steel dissimilar metal pipe/bar with a multi-layer multi-mode characteristic is characterized in that the welding interface obtained from a magnesium side to a steel side comprises three layers, namely a Mg-Zn layer, a Zn layer and a Fe-Zn layer, wherein the average grain size of the Mg-Zn layer is smaller than 2 mu m, a MgZn precipitated phase is contained in the Mg-Zn layer, the size of the precipitated phase is smaller than 100nm, the average grain size of the Zn layer is smaller than 2 mu m, the Fe-Zn layer contains an iron-zinc compound transition phase, and the thicknesses of the Mg-Zn layer, the Zn layer and the Fe-Zn layer are respectively 10-40 mu m, 1-4 mu m and 4-16 mu m.
2. A method of welding a magnesium/steel dissimilar metal tube/bar weld interface having multi-layer, multi-modal characteristics as set forth in claim 1, comprising the steps of:
S1, cleaning a base metal, namely polishing and cleaning the section of a welded magnesium, steel base metal pipe or rod;
S2, preparing an intermediate layer, namely forming a Zn-Mg composite intermediate layer by pure Zn and pure Mg according to the arrangement sequence of Zn/Mg/Zn;
s3, fixing a welded component, namely placing the cleaned parent metal and a Zn-Mg composite intermediate layer on a workbench of a rotary ultrasonic welder, forming a butt joint structure under magnesium upper steel, and placing the Zn-Mg composite intermediate layer in the center of a parent metal butt joint region;
S4, welding, namely performing rotary ultrasonic welding on the fixed welded component, wherein ultrasonic parameters are that the output frequency is 20kHz, the working power is 1000-5000W, the amplitude is 10-50 mu m, and the whole process is divided into three stages, namely, the first stage is 0.5-2S, and the rotating speed is 500-1000 r/min; the second stage is 2-4S, the rotating speed is 1000-2000 r/min, the third stage is 4-5S, and the rotating speed is 100-500 r/min, so as to obtain a pipe/bar butt welding piece;
and S5, short-time annealing, namely annealing the obtained pipe/bar butt welding piece to obtain the magnesium/steel dissimilar metal pipe/bar welding interface with multi-layer multi-mode characteristics.
3. The welding method according to claim 2, wherein in S1, magnesium is selected from any one of Mg-Al, mg-Zn, mg-Mn, mg-Zr, and Mg-RE series, and steel is selected from any one of carbon steel, alloy steel, and high alloy steel.
4. The welding method according to claim 2, wherein in S1, the base metal magnesium and steel are both tubular or rod-shaped, the inner diameter of the pipe is 4.5mm to 28mm, the outer diameter is 6mm to 30mm, the length is 10 to 40mm, the difference between the inner diameter and the outer diameter is 1.5 to 5mm, the diameter of the bar is 3 to 15mm, the length is 10 to 40mm, and the inner diameter and the outer diameter or the diameter of the magnesium and steel are the same.
5. The welding method according to claim 4, wherein in S2, the zn—mg composite intermediate layer has the same inner and outer diameters as magnesium and steel.
6. The welding method according to claim 2, wherein in S4, the triggering condition of the rotational ultrasonic welding is that the pressure head reaches 0.4MPa for the base material to be welded.
7. The welding method according to claim 2, wherein in S5, the annealing temperature is 150 to 220 ℃ and the time is 20min to 1h.
8. The magnesium/steel dissimilar metal tube/bar weldment obtained by the welding method according to any one of claims 2 to 7, wherein the tensile strength of the weldment reaches more than 120 MPa.
9. Use of the magnesium/steel dissimilar metal tube/bar weldment of claim 8 in automotive industry workpieces, aerospace workpieces, and electronics.
10. The use of claim 9, wherein the automotive industry parts include door frames, engine brackets, aerospace parts include seat frames, aircraft wings, landing gear, and electronics products include notebook computer housings, brackets, cell phone midframes.
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