CN110280880A - 6061-T6 aluminium alloy and the high-strength steel dissimilar alloy resistance spot welding method of TRIP980 - Google Patents
6061-T6 aluminium alloy and the high-strength steel dissimilar alloy resistance spot welding method of TRIP980 Download PDFInfo
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- CN110280880A CN110280880A CN201910594767.4A CN201910594767A CN110280880A CN 110280880 A CN110280880 A CN 110280880A CN 201910594767 A CN201910594767 A CN 201910594767A CN 110280880 A CN110280880 A CN 110280880A
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- strength steel
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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
- B23K11/00—Resistance welding; Severing by resistance heating
- B23K11/10—Spot welding; Stitch welding
- B23K11/11—Spot 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
- B23K11/00—Resistance welding; Severing by resistance heating
- B23K11/16—Resistance welding; Severing by resistance heating taking account of the properties of the material to be welded
- B23K11/18—Resistance welding; Severing by resistance heating taking account of the properties of the material to be welded of non-ferrous metals
- B23K11/185—Resistance welding; Severing by resistance heating taking account of the properties of the material to be welded of non-ferrous metals of aluminium or aluminium alloys
-
- 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
- B23K11/00—Resistance welding; Severing by resistance heating
- B23K11/34—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
- B23K2103/20—Ferrous alloys and aluminium or alloys thereof
Abstract
The present invention discloses 6061-T6 aluminium alloy and the high-strength steel dissimilar alloy resistance spot welding method of TRIP980, and the welding condition of resistance spot welding is as follows: welding current 6.5kA-10.5kA, weld interval 15cyc-60cyc, electrode pressure 1kN-3.5kN.The addition of Cu can effectively improve the plasticity and toughness of its connector under conditions of improving bond pull power, and fracture mode is button fracture, be in tough crisp mixed fracture, increase butt joint preheating step, reduce postwelding cooling velocity, reduce welding stress；On the other hand the plasticity of metal can be improved in the increase of pre- thermocurrent, makes workpiece be easy to fit closely, prevents from splashing, prevent the appearance of crackle, is conducive to the raising of tack-weld mechanical property.
Description
Technical field
The present invention relates to metal welding machine technical fields.Specifically 6061-T6 aluminium alloy and TRIP980 high-strength steel xenogenesis
Resistance alloys spot welding method.
Background technique
In recent years since the problems such as energy crisis is with vehicle exhaust discharge quantity is increasingly serious, automotive light weight technology is got over by people
Carry out more concerns.Wherein, it is that automotive light weight technology develops important research direction that aluminium alloy is connect with high-strength steel.However for two
For person, since the immiscible property of metallurgy leads to interface thick and crisp Fe-Al intermetallic compound easily generated, to be degrading connector
Mechanical property.In this regard, researcher has inquired into laser soldering, explosion weldering, agitating friction weldering etc. it is new be suitable for aluminum/steel dissimilar
Connection method, but due to limiting the extensive use of these technologies in terms of the applicability of cost and technology
Resistance spot welding has many advantages, such as at low cost, high degree of automation, is the main welding side of current automotive body sheet
Method.In order to realize energy-saving and emission-reduction, Chong Yuliang et al. has carried out resistance spot welding examination to the high-strength dual phase steel of DP590 and 6061 aluminium alloys
It tests, connector maximum stretching force reaches 3kN, is broken in aluminum mother plate side.Shi Hongxin et al. has carried out aluminium alloy with stainless steel different
Kind welding, shows that interfacial reaction layer can weaken connector tensile strength.But if aluminium/steel directly carries out dissimilar welding, process window
Mouth range is small, and welding quality is not easy to control, and connector brittleness is big.And intermediate course is used, it can be to aluminum/steel dissimilar joint performance
It has some improvement.Oikawa et al. et al. uses the aluminium steel plated of 0.77mm as interlayer, uses the stretching of composite plate
Performance is far longer than tensile property without dissection.I.Ibrahim et al. et al. austenitic stainless steel and 6061 aluminium alloys it
Between be attached using the Al-Mg middle layer of 80um, connector realizes good connection.But there are still interlayer it is at high cost,
And aluminium alloy and high-strength steel xenogenesis tack-weld brittleness are big, the problems such as poor mechanical property.
Summary of the invention
For this purpose, technical problem to be solved by the present invention lies in provide a kind of improvement connector plasticity and toughness, increase drawing force
6061-T6 aluminium alloy and the high-strength steel dissimilar alloy resistance spot welding method of TRIP980.
In order to solve the above technical problems, the invention provides the following technical scheme:
6061-T6 aluminium alloy and the high-strength steel dissimilar alloy resistance spot welding method of TRIP980, the welding condition of resistance spot welding is such as
Under: welding current 6.5kA-10.5kA, weld interval 15cyc-60cyc, electrode pressure 1kN-3.5kN.
Above-mentioned 6061-T6 aluminium alloy and the high-strength steel dissimilar alloy resistance spot welding method of TRIP980, the welding item of resistance spot welding
Part is as follows: welding current 9.5kA, weld interval 35cyc, electrode pressure 1.5kN.
Above-mentioned 6061-T6 aluminium alloy and the high-strength steel dissimilar alloy resistance spot welding method of TRIP980, in 6061-T6 aluminium alloy
Pure copper sheet is overlapped between TRIP980 high-strength steel or surface is coated with the pure copper sheet of lanthanum powder or gadolinium powder and lanthanum powder.
Above-mentioned 6061-T6 aluminium alloy and TRIP980 high-strength steel dissimilar alloy resistance spot welding method are coated with lanthanum in pure copper sheet
The side of the mixed-powder of powder or gadolinium powder and lanthanum powder is towards TRIP980 high-strength steel.
Above-mentioned 6061-T6 aluminium alloy and the high-strength steel dissimilar alloy resistance spot welding method of TRIP980, the coated weight of lanthanum powder are
The 0.15-0.3% of copper sheet quality；The coated weight of the mixed-powder of gadolinium powder and lanthanum powder is the 0.1-0.2% of copper sheet quality, gadolinium
The mass ratio of powder and lanthanum powder is 1:(5-10).
Above-mentioned 6061-T6 aluminium alloy and the high-strength steel dissimilar alloy resistance spot welding method of TRIP980, pure copper sheet overlapped length
More than or equal to 30mm, using the burr on angle grinder removal 6061-T6 aluminium alloy and TRIP980 high-strength steel side before welding, and sand is used
Paper removes surface film oxide, then with dehydrated alcohol and acetone wiping surface impurity and greasy dirt.
Above-mentioned 6061-T6 aluminium alloy and the high-strength steel dissimilar alloy resistance spot welding method of TRIP980 also need pair before welding
Plumb joint is preheated；The condition that butt joint is preheated are as follows: pre- thermocurrent is 6kA-8kA；Preheating time is 10-20cyc.
Above-mentioned 6061-T6 aluminium alloy and the high-strength steel dissimilar alloy resistance spot welding method of TRIP980, the welding item of resistance spot welding
Part is as follows: welding current 15kA-17kA, weld interval 10cyc-20cyc, electrode pressure 1kN-3.5kN.
Above-mentioned 6061-T6 aluminium alloy and the high-strength steel dissimilar alloy resistance spot welding method of TRIP980, butt joint are preheated
Condition are as follows: pre- thermocurrent be 6kA-8kA, preheating time 10-20cyc；The welding condition of resistance spot welding is as follows: welding current
For 15kA-17kA, weld interval 10cyc-20cyc, electrode pressure 1kN-3.5kN.
Above-mentioned 6061-T6 aluminium alloy and the high-strength steel dissimilar alloy resistance spot welding method of TRIP980, butt joint are preheated
Condition are as follows: pre- thermocurrent be 8kA, preheating time 20cyc；The welding condition of resistance spot welding are as follows: welding current 16kA, weldering
Connecing the time is 20cyc, electrode pressure 2.7kN.
Technical solution of the present invention achieves following beneficial technical effect:
(1) addition of Cu changes intermetallic compound ingredient, has replaced the Fe element of a part of Fe-Al electronics centering,
Fe-Al-Cu ternary compound is formed, good comprehensive performance is made it have, improves connector brittleness.The addition of Cu connects in raising
The plasticity and toughness of its connector can effectively be improved under conditions of head drawing force, fracture mode is button fracture, disconnected in tough crisp mixing
It splits.
(2) before welding, butt joint preheating step is increased, postwelding cooling velocity is reduced, reduces welding stress；It is another
The plasticity of metal can be improved in the increase of the pre- thermocurrent of aspect, and workpiece is made to be easy to fit closely, and prevents from splashing, and prevents going out for crackle
It is existing, be conducive to the raising of tack-weld mechanical property.
It (3) is 8kA in pre- thermal parameter, 20cycle, welding current, weld interval, electrode pressure is respectively 16kA,
It is 4.34kN that drawing force, which reaches maximum value, under the conditions of 20cycle, 2.7kN, improves 14% compared with copper sheet is not added with.
(4) copper sheet surface coating lanthanum powder or the mixed-powder of gadolinium powder and lanthanum powder is coated, not only changed between metal
Chemical composition, more importantly when can improve the crystallization condition of TRIP980 high-strength steel side and reduce molten bath crystallization
Thermal stress, to reduce the crystallization condition difference of 6061-T6 aluminium alloy side and TRIP980 high-strength steel side and reduce weld seam
Locate the generation of crackle, and lanthana and lanthanum itself also have the function of refinement crystal grain, the reason of these two aspects, makes weld seam two sides
Crystal grain uniformly refines；The TRIP980 high-strength steel side crystallization condition that gadolinium-doped powder helps to strengthen lanthanum and lanthana improve and
Grain Refinement Effect, so that drawing force greatly improved.
Detailed description of the invention
Connector of Fig. 1-1 6061-T6 aluminium alloy of the present invention from the high-strength steel dissimilar alloy of TRIP980 under different welding currents
Interface surface pattern；(a) welding current be 6.5kA, TRIP980 high-strength steel joint interface surface topography, (b) welding current be
6.5kA, 6061-T6 aluminum alloy joint interface surface pattern, (c) welding current is 10.5kA, TRIP980 high-strength steel joint interface
Surface topography, (d) welding current is 10.5kA, 6061-T6 aluminum alloy joint interface surface pattern；
Connector of Fig. 1-2 6061-T6 aluminium alloy of the present invention from the high-strength steel dissimilar alloy of TRIP980 under different welding currents
Surface topography；(a) welding current is 7kA, and TRIP980 high-strength steel joint surface pattern, (b) welding current is 7kA, 6061-T6
Aluminum alloy joint surface topography, (c) welding current is 10.5kA, TRIP980 high-strength steel joint surface pattern, (d) welding current
For 10.5kA, 6061-T6 aluminum alloy joint surface topography；
Steel under different welding currents of Fig. 1-3 6061-T6 aluminium alloy of the present invention and the high-strength steel dissimilar alloy of TRIP980/
The impression diameter figure of aluminium two sides；
Steel under different welding currents of Fig. 1-4 6061-T6 aluminium alloy of the present invention and the high-strength steel dissimilar alloy of TRIP980/
Spot welding aluminum connector cross section macro morphology: (a) welding current 7.5kA, (b) welding current 9.5kA, (c) welding current 10.5kA；
Fig. 1-5 6061-T6 aluminium alloy of the present invention is molten under different welding currents from the high-strength steel dissimilar alloy of TRIP980
Nuclear diameter；
Fig. 1-6 6061-T6 aluminium alloy of the present invention and TRIP980 high-strength steel dissimilar alloy welding electric current are to steel/aluminium xenogenesis point
The influence of plumb joint drawing force；
Fig. 1-7 6061-T6 aluminium alloy of the present invention steel/aluminium under different weld intervals from the high-strength steel dissimilar alloy of TRIP980
The surface topography of tack-weld: (a) weld interval 20cyc, TRIP980 high-strength steel joint surface pattern, (b) weld interval
20cyc, 6061-T6 aluminum alloy joint interface surface pattern, (c) weld interval 35cyc, TRIP980 high-strength steel joint surface shape
Looks, (d) weld interval 35cyc, 6061-T6 aluminum alloy joint interface surface pattern, (e) weld interval 60cyc, TRIP980 high
Strong steel joint surface pattern, (f) weld interval 60cyc, 6061-T6 aluminum alloy joint interface surface pattern；
Fig. 1-8 6061-T6 aluminium alloy of the present invention steel/aluminium under different weld intervals from the high-strength steel dissimilar alloy of TRIP980
The impression diameter of two sides；
Fig. 1-9 6061-T6 aluminium alloy of the present invention steel/aluminium under different weld intervals from the high-strength steel dissimilar alloy of TRIP980
Tack-weld cross section macro morphology: (a) 15cyc, (b) 30cyc, (c) 50cyc；
Fig. 1-10-1 6061-T6 aluminium alloy of the present invention is from the high-strength steel dissimilar alloy of TRIP980 under different weld intervals
Nugget size；
Fig. 1-10-2 6061-T6 aluminium alloy of the present invention and the high-strength steel dissimilar alloy of TRIP980 different weld intervals to steel/
The influence of aluminium xenogenesis tack-weld drawing force；
Fig. 1-11 6061-T6 aluminium alloy of the present invention and the high-strength steel dissimilar alloy of TRIP980 steel/aluminium under Different electrodes pressure
The surface topography of tack-weld: (a) electrode pressure is 1kN, TRIP980 high-strength steel joint interface surface topography, (b) electrode pressure
For 1kN, 6061-T6 aluminum alloy joint interface surface pattern, (c) electrode pressure is 3.5kN, TRIP980 high-strength steel joint interface
Surface topography, (d) electrode pressure is 3.5kN, 6061-T6 aluminum alloy joint interface surface pattern；
Fig. 1-12-1 6061-T6 aluminium alloy of the present invention and the high-strength steel dissimilar alloy of TRIP980 under Different electrodes pressure steel/
The impression diameter of spot welding aluminum connector；
Fig. 1-12-2 6061-T6 aluminium alloy of the present invention and the high-strength steel dissimilar alloy of TRIP980 under Different electrodes pressure steel/
Spot welding aluminum connector cross section macro morphology: (a) 1kN, (b) 1.5kN, (c) 3kN；
Fig. 1-13 6061-T6 aluminium alloy of the present invention and the high-strength steel dissimilar alloy of TRIP980 are molten under Different electrodes pressure
Nuclear diameter；
Fig. 1-14 6061-T6 aluminium alloy of the present invention is with the high-strength steel dissimilar alloy of TRIP980 in Different electrodes pressure to steel/aluminium
The influence of xenogenesis tack-weld drawing force；
Welding current pair after overlap joint fine copper between Fig. 2-1 6061-T6 aluminium alloy of the present invention and the high-strength steel dissimilar alloy of TRIP980
The influence of tack-weld drawing force and nugget size；
Fig. 2-2 6061-T6 aluminium alloy of the present invention and different welding after overlap joint fine copper between the high-strength steel dissimilar alloy of TRIP980 are electric
The tack-weld interface topography flowed down: when (a) welding current is 15kA, aluminium/steel tack-weld interface topography,
Fig. 2-3 6061-T6 aluminium alloy of the present invention and different welding after overlap joint fine copper between the high-strength steel dissimilar alloy of TRIP980 are electric
The tack-weld interface topography flowed down: when (b) welding current is 17kA, aluminium/steel tack-weld interface topography；
Pre- thermocurrent after overlap joint fine copper between Fig. 2-4 6061-T6 aluminium alloy of the present invention and the high-strength steel dissimilar alloy of TRIP980
The influence of difference welding current butt joint drawing force and nugget size when 5kA, preheating time 20cycle；
Fig. 2-5 6061-T6 aluminium alloy of the present invention between the high-strength steel dissimilar alloy of TRIP980 overlap fine copper after different welding when
Between to the influence of aluminium/steel tack-weld mechanical property and nugget size；
Pre- thermocurrent is after overlapping fine copper between Fig. 2-6 6061-T6 aluminium alloy of the present invention and the high-strength steel dissimilar alloy of TRIP980
6kA, preheating time 20cycle, welding parameter are respectively welding current 16kA, weld interval 20cycle, electrode pressure 1.5kN
Under aluminium/steel tack-weld interface topography figure；
Fig. 2-7 6061-T6 aluminium alloy of the present invention between the high-strength steel dissimilar alloy of TRIP980 overlap fine copper after different pre- thermoelectricity
Stream is to the influence of aluminium/steel tack-weld drawing force and nugget size；
Different electrodes pressure after overlap joint fine copper between Fig. 3 6061-T6 aluminium alloy of the present invention and the high-strength steel dissimilar alloy of TRIP980
To the influence of aluminium/steel tack-weld drawing force and nugget size；
Pre- thermocurrent 8kA after overlap joint fine copper between Fig. 4 6061-T6 aluminium alloy of the present invention and the high-strength steel dissimilar alloy of TRIP980,
Preheating time 20cycle, welding current, weld interval, electrode pressure are respectively 16kA, the aluminium under 20cycle, 2.7kN/steel point
Tack-weld interface topography.
Specific embodiment
1 welding condition of embodiment is to the influence of aluminium/steel tack-weld mechanical property
Diameter is the circular cone ordinary telegram cartridge of 8mm, and foundation single factor test rule has studied welding current, weld interval, electricity respectively
Extreme pressure power is to the influence of steel/spot welding aluminum joint mechanical property.In experimentation, 3 samples, guarantee test are welded under every group of parameter
As a result stability.6061-T6 aluminium alloy and TRIP980 high-strength steel xenogenesis are determined according to the size of drawing force and welding quality
More excellent parameter under the conditions of resistance spot welding.
The influence of 1.1 welding currents
Under the stable condition for keeping weld interval (30cyc) and electrode pressure (2kN), welding current (6.5- is had studied
10.5kA) to the influence of steel/aluminium xenogenesis joint mechanical property.
1.1.1 the influence of welding current butt joint tissue
Fig. 1-1 is the joint interface surface topography under different welding currents.As shown in Fig. 1-1 (a), (b), work as welding current
When for 6.5kA, interface Forming Quality is good, generates without nugget splash, is observed that significantly at aluminium alloy interface
Plastic area, effectively preventing influences (oxidized aluminum alloy) caused by appearance of weld process as extraneous factor；When welding electricity
When stream is increased to 10.5kA, as shown in Fig. 1-1 (c), (d), due to the substantial increase of heat input, welding region temperature is increased, is led
Steel aluminium joint Surface yield strength is caused to reduce, aluminium alloy melts and expands rapidly, molten aluminium alloy under the action of electrode pressure
It is extruded, interface a large amount of splash occurs and goes out plastic area, and with aluminium alloy splash and viscous glutinous phenomenon, seriously
Affect the mechanical property of connector.
Fig. 1-2 is the shape appearance figure of the joint surface under different welding currents.It is found that welding current is to impression from figure
Diameter plays very important influence.As shown in Fig. 1-2 (a), (b), when welding current is 7kA, the impression of aluminium alloy side
Diameter is 4.675mm, and the impression diameter of high-strength steel side is 4.135mm.With the increase of welding current, the pressure of aluminium alloy side
Trace diameter increasing degree greatly improves, and the impression diameter of high-strength steel side is also increasing, but without the obvious of aluminium alloy side.Such as
Shown in Fig. 1-2 (c), (d), when welding current increases to 10.5kA, the impression diameter of aluminium alloy side is increased to 7.445mm, high
The impression diameter of strong steel side is 6.375mm.On the whole, since aluminium alloy is under the action of Thermal Cycle, with electrode tip
The surface temperature to contact with each other increases, and yield strength decline is obvious, and the effect for causing aluminum alloy surface to resist electrode pressure reduces,
And the elongation percentage of aluminium alloy at high temperature is greater than high-strength steel, under the action of electrode pressure and electrode head surface, impression diameter
Increase trend is more obvious；It is unobvious to review yield strength downward trend under the action of Thermal Cycle of high-strength steel side,
Under the action of electrode pressure, depth of cup is almost nil, and there are significantly viscous copper and oxidation in surface.Therefore, aluminium alloy side
Impression diameter is greater than the impression diameter of high-strength steel side, but overall depth of cup is unobvious, and surface forming quality is good.Fig. 1-
3 be steel/aluminium two sides impression diameter under different welding currents.
Fig. 1-4 is steel/spot welding aluminum connector cross section macro morphology under different welding currents.It can be seen from the figure that with
The increase of welding current, nugget size are gradually increased, and nugget height is consequently increased, and increase to 10.5kA from the 0.7mm of 7.5kA
1.53mm.When electric current is 7.5kA, since thermal weld stress is small, the aluminium alloy volume of melting is also smaller, causes aluminium alloy molten
Nuclear diameter and nugget height are also smaller；When welding current rises to 10.5kA, heat input increases sharply, and aluminium alloy melts body
Product also increases accordingly, and aluminium alloy nugget size and nugget height is caused apparent increase occur.From Fig. 1-4 (c) figure also
It can be found that TRIP980 high-strength steel side occur steel plate convex, closer from solder joint center, steel plate convex degree is bigger, with away from
Remoter from solder joint center, interface is gradually smoothened.Such phenomenon may be solder joint center when melting since aluminium alloy is heated
Domain temperature highest, aluminium alloy is heated to be melted, and aluminium alloy side yield strength is caused to be substantially reduced；One side surface of steel keeps solid at this time
Body state generates the phenomenon that protrusion arrives aluminium alloy side due to expanded by heating under the action of electrode pressure.Under normal circumstances,
The drawing force of steel spot welding aluminum is mainly determined by nugget size and nugget height, but working as welding current increases to after 10kA,
Occur apparent aluminium alloy splash phenomena at joint interface, leads to the mechanical properties decrease of connector, while there are also crackles, shrinkage cavity
The defects of generate, be unfavorable for the molding of weld seam.
Fig. 1-5 is the nugget size under different welding currents.It can be seen that the increase with welding current, weldering from Fig. 1-5
It connects heat input also to increase accordingly, more aluminium alloys participate in fusing, aluminum alloy melting under identical electrode pressure, weld interval
Volume increases, and nugget size is caused to increase.In 6.5-9.5kA, the linear ratio of nugget size increases, and joint mechanical property is flat
It is steady to rise.But when welding current is in 9.5-10.5kA, there is the trend of precipitous rising in nugget size, although molten in 10.5kA
It is 6.265mm that nuclear diameter, which reaches maximum value, considerably beyond the required standard of nugget size in overlapping mode(use Europe
Continent nugget size required standard, t are lamella thickness), but the aluminium alloy of interface is also brought while nugget size increase
The generation of splash and shrinkage cavity crack defect greatly reduces the mechanical property of connector.
1.1.2 the influence of welding current butt joint mechanical property
Table 1-1 is steel/spot welding aluminum connector stretch test result under different welding currents.Test result shows: keeping
In the case that weld interval, electrode pressure are constant, as welding current increases, connector shearing resistance is consequently increased.When welding electricity
When stream reaches 9.5kA, bond pull power reaches maximum value (3.33kN).When reaching 10.5kA when further increasing welding current, connect
Head drawing force drops to 2.082kN.The influence of welding current butt joint mechanical property mainly and nugget size, intermetallic compounds layer
Thickness and the welding defect as caused by heat input it is related.Welding current is in 6.5~9.5kA, with the increasing of heat input
Adding makes more aluminium alloys participate in fusing, and nugget size increases, and bond pull power is consequently increased.Further increase welding current
(9.5-10.5kA), nugget size increase, but since a large amount of heat input leads to the thickness increasing of compound layer between interface metal
Add, splashing occurs in steel/aluminium interface, and reduces the mechanical property of weld seam, therefore drawing force reduces.
The drawing force of table 1-1 difference welding current lower contact
According to the result of welding current butt joint mechanical property it is found that under this experimental condition, as shown in figures 1 to 6,9.5kA
Welding current be conducive to improve connector mechanical property.
The influence of 1.2 weld intervals
Under the stable condition for keeping welding current (9.5kA) and electrode pressure (2kN), weld interval is studied to steel/aluminium
The influence of xenogenesis joint mechanical property.
1.2.1 the influence of weld interval butt joint tissue
Fig. 1-7 shows steel under different weld intervals/spot welding aluminum joint surface pattern photo.From can in Fig. 1-7
Out, weld interval has a significant effect to the impression diameter of steel aluminium xenogenesis resistance spot welding.In welding current (9.5kA), electrode pressure
Under conditions of (2kN) is remained unchanged, when soldered between when being 20cyc, the impression diameter of aluminium alloy side is 5.76mm, high-strength steel
The impression diameter of side is 4.755mm；, when soldered between when increasing to 35cyc, the impression diameter of aluminium alloy side is
7.45mm, the impression diameter of high-strength steel side are 5.35mm；With the increase of weld interval, thermal weld stress is significantly increased, together
When steel aluminium two sides yield strength decline, when soldered between when being 60cyc, the impression diameter of aluminium alloy side is 8.5mm, high-strength
The impression diameter of steel side is 6.75mm.But by subsequent experimental observation it is recognized that while with weld interval increase, weldering
It connects heat input to significantly increase, under identical electrode pressure, liquid aluminium alloy reduces the anti-pressure ability of electrode pressure, aluminium alloy
The depth of cup of side increases；Since solid state is held in one side surface of steel, although the raising of welding region temperature results in steel side
Yield strength decline, but the anti-pressure ability that electrode pressure is resisted in steel side is not reduced, therefore the depth of cup of steel side
Degree has little effect.
For this purpose, introducing the general of impression rate λ to better illustrate the influence degree of aluminium alloy side tack-weld impression
It reads, calculation is as follows:
λ=H0/H1
(wherein H0Indicate the depth of cup of aluminium alloy side, H1Indicate the thickness of aluminium alloy base material)
When being 15cyc between when soldered, the depth of cup of aluminium alloy side is 0.12mm, and impression is calculated using formula
Rate is 6%；Weld interval rises to 30cyc, and aluminium alloy side depth of cup increases to 0.13, and increasing degree is unobvious, at this time impression
Rate is 6.5%；As weld interval further increases, according to Joule's law Q=I2Rt, when electrode pressure is constant, electrode tip
Contact area between steel aluminium two sides and steel aluminium is constant, resistance holding be basically unchanged, welding current under the same conditions,
Weld interval is longer, and the temperature of welding region is also higher, and the depth of cup of aluminium alloy side is also just more obvious at this time.When welding
Between when increasing to 60cyc, the depth of cup of aluminium alloy side is 1.6mm, and impression rate is 17%, and variation tendency is more obvious.According to
Joint for resistance spot welding quality control standards (QCS), weld indentation rate are not to be exceeded 30%, excessive impression rate will affect surface quality with
And joint mechanical property.Influence of the weld interval to steel spot welding aluminum connector impression rate is mainly due to the variation of thermal weld stress.
Fig. 1-8 shows the impression diameter of the steel aluminium two sides under different weld intervals.
Fig. 1-9 shows steel under different weld intervals/spot welding aluminum connector cross section macro morphology.Institute from from Fig. 1-9
Know, when soldered between be 15cyc when, nugget size 4.495 melts a height of 0.82mm, and thermal weld stress is smaller at this time, welding temperature
The aluminium alloy small volume melted in degree region, causes nugget size not reach the required standard of steel spot welding aluminum；When soldered
Between when being further increased to 30cyc, with the increase of thermal weld stress, aluminum alloy melting volume increases, and nugget size reaches
5.625mm melts a height of 0.94mm, has exceeded European Union and provides the nugget size standard of steel spot welding aluminum, but melts high increasing degree not
Obviously；With continuing to increase for weld interval, under conditions of electrode pressure and welding current remain unchanged, thermal weld stress
Increase rapidly, aluminum alloy melting volume further increases, when soldered between when being 50cyc, nugget size reaches 5.99mm, melts height
For 1.44mm, increasing degree is more obvious.Influence of the weld interval for steel spot welding aluminum connector nugget size is also mainly due to
The variation of thermal weld stress.Fig. 1-10 shows the nugget size under different weld intervals.
1.2.2 the influence of weld interval butt joint mechanical property
Table 1-3 is steel/spot welding aluminum connector stretch test result under different weld intervals.Test result shows: keeping
Welding current, in the case that electrode pressure is constant, when soldered between be 10cyc when, bond pull power be 2.021kN, with weldering
The increase of time is connect, bond pull power is consequently increased, and weld interval reaches maximum stretching force 3.4kN when being 35cyc.Further
Increase weld interval, bond pull power declines therewith, when soldered between when being 50cyc, be down to 1.921kN.Weld interval is in 10-
When 35cyc, the increase of bond pull power is mainly related with the increase of nugget size.As weld interval further increases, welding
Connect electric current, in the case that electrode pressure remains unchanged, thermal weld stress also increases accordingly (Q=I2RT), Fe/Al member between interface
It being known as more sufficient time and participates in diffusion, interface generates the intermetallic compound with labyrinth, and thickness increases,
During carrying out tension test, hard crisp intermetallic compound leads to the decline of joint mechanical property.
The drawing force of the different weld interval lower contacts of table 1-3 is according to the result of weld interval butt joint mechanical property
By Fig. 1-11 it is found that under this experimental condition, the weld interval of 35cyc is conducive to improve steel/aluminium xenogenesis connector
Tensile property.
The influence of 1.3 electrode pressures
Under holding welding current (9.5kA), the experimental condition of weld interval (35cyc), Electrode pressure is different to steel/aluminium
The influence of kind joint mechanical property.
1.3.1 the influence of electrode pressure butt joint tissue
Electrode pressure is the important parameter for changing thermal weld stress indirectly.This section keeps welding current (9.5kA), weldering
Under the primary condition for meeting time (35cyc), by changing electrode pressure (1-3.5kN), has studied electrode pressure and weld seam is connect
The influence of head surface quality and nugget size.Electrode pressure is smaller, and contact area is smaller between steel/aluminium interface, according to formula R
=ρ × l/s, interface contact resistance is bigger, leads to the direct increase of thermal weld stress.Fig. 1-11 is shown under Different electrodes pressure
Steel/spot welding aluminum connector show pattern.It can be seen from the figure that, by Fig. 1-11 (a), (b), aluminium closes when electrode pressure is 1kN
Golden side impression diameter is 7.505mm, is irregular ellipse, and high-strength steel side size reaches 6.745mm, is welding
Cheng Zhongyou spark generates, and with a large amount of splashes；When electrode pressure increases to 3.5kN, by Fig. 1-11 (c), (d), aluminium alloy
The impression diameter of side is decreased to 6.68mm, and regular circle is presented, and high-strength steel side impression diameter is decreased to 4.225mm, together
When do not have spark and welding splash generate.The reason of generating this phenomenon, mainly due to when electrode pressure is too small, between interface
Contact resistance becomes larger, so that thermal weld stress increases significantly, more aluminum alloy meltings under identical weld interval and electric current,
Liquid aluminium alloy goes out plastic area and produces nugget splashing simultaneously, increases the impression diameter of joint surface；Similarly, when electrode pressure
When power increases, the heat between steel/aluminium is reduced, and the liquid aluminium alloy for participating in fusing is also reduced therewith, therefore leads to joint surface
Impression diameter reduces.Fig. 1-12 shows steel/aluminium joint surface indentation diameter under Different electrodes pressure.
Fig. 1-13 shows the nugget size under Different electrodes pressure.It can be seen from the figure that when electrode pressure is 1kN
When, nugget size reaches maximum value 6.5mm (shown in Fig. 1-12 (a)), melts a height of 1.29mm at this time.
With the increase of electrode pressure, thermal weld stress also reduces therewith.When electrode pressure is 1.5kN, nugget size
For 6.16mm, melting high but increase is 1.62mm.The reason of such phenomenon is the sweating heat due to as electrode pressure minimum 1kN
The anti-pressure ability of liquid aluminium alloy also reduces therewith while input increases, and more aluminium alloys participate in fusing, far beyond
The ability of plasticity ring protection, therewith caused by the result is that nugget splashes, and, there is a large amount of sparks, interface and nugget in while welding
There is the generation of the welding defects such as shrinkage cavity in inside, melts high reduce.
When electrode pressure is larger (3kN), nugget size at this time is decreased to 5.41mm, and molten height substantially reduces.To sum up institute
It states, electrode pressure is mainly due to the variation of thermal weld stress to the influence of nugget size.Fig. 1-13 shows Different electrodes pressure
Nugget size under power.
1.3.2 the influence of electrode pressure butt joint mechanical property
Table 1-4 is steel/spot welding aluminum connector stretch test result under Different electrodes pressure.Test result shows: welding
Electric current, weld interval stablize under the experimental condition of 9.5kA, 35cyc, and steel/aluminium xenogenesis connector drawing force is with electrode pressure
Increase present first increase after slowly reduce until stable trend.When electrode pressure is 1kN, bond pull power is 3.17kN.
Since lesser electrode pressure causes interfacial contact area to sharply increase, according toInterfacial contact area reduces, electricity
Resistance increases, thus generates a large amount of resistance heat.Excessive heat input causes nugget to splash, and the welding defects such as shrinkage cavity greatly drop
The low mechanical property of connector.With the increase of electrode pressure, it is 3.793kN that maximum value is reached when electrode pressure is 1.5kN,
Welding quality is good, has reached good welding effect.Electrode pressure is further increased, steel/aluminium xenogenesis bond pull power is slow
Decline is until stablize the level in 3.1-3.2kN.It on the one hand is the increase due to electrode pressure, thermal weld stress also drops therewith
It is low, it causes nugget size to reduce, reduces the mechanical property of connector；On the other hand in experimental observation, when electrode pressure increases
Nugget size has almost no change when being added to 2.5kN or more, causes the tensile property of rear several experimental design parameters unobvious
Variation.
The drawing force of table 1-4 Different electrodes pressure lower contact
By Fig. 1-14 it is found that under this experimental condition, the electrode pressure of 1.5kN is conducive to improve steel/aluminium xenogenesis connector
Tensile property.
In conclusion in welding condition are as follows: when welding current 9.5kA, weld interval 35cyc, electrode pressure 1.5kN, have
Conducive to the mechanical property for improving connector, be conducive to improve steel/aluminium xenogenesis connector tensile property.
2 Cu of embodiment is to the influence of aluminium/steel tack-weld mechanical property
The present embodiment has studied welding current, weld interval, electrode pressure to aluminium/steel tack-weld mechanical property respectively
It influences, according to the factors such as the size of drawing force and joint surface forming quality, so that it is determined that more excellent parameter, and illustrate to be spot welded
Head rupture mechanism.
2.1.1 welding current is to the influence of aluminium/steel tack-weld mechanical property
Since the addition of copper sheet increases thermal weld stress, bigger welding parameter is selected just to be able to achieve effective weldering
It connects.Compared to copper sheet is not added, the welding current of 10-17kA is successively used, keeps electrode pressure 1.5kN, weld interval 20cycle
It is constant.Find that the tack-weld drawing force at 10~14kA of welding current is less than 1kN during the experiment, sample is unqualified.
When welding current increases to as 15~17kA, tack-weld drawing force increases, and Fig. 2-1 is that welding current draws tack-weld
The influence of stretch and nugget size.
By Fig. 2-1 it is found that bond pull power increases to 1.905kN when welding current is 16kA, welded with further increasing
Heat input is connect, when welding current is 17kA, bond pull power is down to 1.623kN, and nugget size overall variation trend is unobvious, directly
Diameter maintains 6mm or so, has reached dot weld nugget diameter standard, but bond pull power is not significantly improved but,
Compared with copper sheet not being added to decrease, Fig. 2-3 is the tack-weld interface topography under different welding currents.
By Fig. 2-3 it is found that different degrees of splashing occurs for aluminium/steel tack-weld interface, and aluminium alloy nugget side has
Crackle generates.It on the one hand is since the raising of welding current leads to the increase of thermal weld stress, in the rapid cooling of electrode water cooling
Under the conditions of, so that cooling rear joint has biggish crystalline stress and generates with fire check；On the other hand defeated in biggish heat
Under the conditions of entering, aluminium alloy nugget goes out plastic area, reduces the effective loaded area of connector, causes tack-weld mechanical property
Deteriorate.For this purpose, in order to reduce the problems such as there are biggish thermal stress and welding splash for crystallisation by cooling rear joint, using preheating
Measure improves it, and the pre- thermal parameter of Preliminary design is 5kA, and 20cycle, Fig. 2-4 are using 5kA, the pre- thermal parameter of 20cycle
Influence of the lower difference welding current to tack-weld drawing force and nugget size.
By Fig. 2-4 and Fig. 2-1 comparison it is found that using under pre- thermal parameter bond pull power and nugget size have one
The promotion for determining degree, when welding current is 16kA, bond pull power is 2.585kN, and nugget size reaches 7.2mm, mechanical property
A degree of improvement can be obtained.So preliminary assert under conditions of weld interval 20cycle, electrode pressure 1.5kN, weldering
Connecing electric current is that 16kA can make tack-weld realize good connection.
2.1.2 weld interval is to the influence of aluminium/steel tack-weld mechanical property
This section is being respectively 5kA, 20cycle, 16kA based on pre- thermocurrent, preheating time, welding current, electrode pressure,
Under conditions of 1.5kN, different weld intervals are had studied to the influence of aluminium/steel tack-weld mechanical property.
Fig. 2-5 is different weld intervals to the influence of aluminium/steel tack-weld drawing force and nugget size.As seen from the figure, with
The increase of weld interval, drawing force it is in rising trend with nugget size.When being 20cycle between when soldered, drawing force is
2.585kN, nugget size 7.2mm.But carried out in preheating current parameters Optimum Experiment in the later period, discovery is in weld interval
Preheating parameter optimization process window under 20cycle is small, cannot achieve effective preheating parameter optimization, therefore takes the weld interval to be
Basic parameter of the 15cycle as next step test.Fig. 2-6 is that pre- thermal parameter is 6kA, 20cycle, when welding current, welding
Between, electrode pressure be respectively 16kA, the aluminium under 20cycle, 1.5kN/steel tack-weld interface topography figure.By Fig. 2-6 it is found that working as
Pre- thermal parameter is set to 6kA, and when 20cycle, weld interval is that the tack-weld under 20cycle has and burns phenomenon and generate, and causes
Spot-welding sample failure further illustrates that weld interval is the more excellent parameter that 15cycle is this test.
2.1.3 pre- thermocurrent is to the influence of aluminium/steel tack-weld mechanical property
Based on early-stage study as a result, this section is in preheating time, welding current, weld interval, electrode pressure is respectively
Under conditions of 20cycle, 16kA, 20cycle, 1.5kN, pre- thermocurrent is analyzed to aluminium/steel tack-weld mechanical property shadow
It rings, to further be optimized to pre- thermal parameter.
Fig. 2-7 is different pre- thermocurrents to the influence of aluminium/steel tack-weld drawing force and nugget size.It is analyzed by Fig. 2-7
It can obtain, with the increase of pre- thermocurrent, drawing force is in rising trend, and when pre- thermocurrent is 8kA, tack-weld drawing force is increased to
For 2.754kN.Nugget size variation tendency is unobvious, and average diameter maintains 7.5mm or so.The increase of pre- thermocurrent can have
The reduction postwelding cooling velocity of effect reduces welding stress；On the other hand the plasticity of metal can be improved in the increase of pre- thermocurrent, makes
Workpiece is easy to fit closely, and prevents from splashing, and is conducive to the raising of tack-weld mechanical property.
2.2.4 electrode pressure is to the influence of aluminium/steel tack-weld mechanical property
Based on early-stage study as a result, this section in pre- thermal parameter is 8kA, 20cycle, welding current, weld interval is respectively
On the conditioned basic of 16kA, 20cycle, electrode pressure is had studied to the influence of aluminium/steel tack-weld mechanical property.
Fig. 3 is Different electrodes pressure to the influence of aluminium/steel tack-weld drawing force and nugget size.From the figure 3, it may be seen that with
The increase of electrode pressure, drawing force is in the trend dropped afterwards is first increased, and when electrode pressure is 2.7kN, drawing force increases to 4.34kN, shape
It is broken at button；With electrode pressure is further increased, drawing force is on a declining curve, mainly due to joint surface impression rate with
The increase of electrode pressure also improving, being excessively increased for impression rate further reduced tack-weld receiving during stretching
The effective area of load, causes drawing force to decline.Nugget size is in reduction trend with the increase nugget size of electrode pressure, but
Amplitude of variation is smaller, and main cause is attributed to heat input and is reducing.Electrode pressure increases, and the reduction of practical contact resistance causes
Thermal weld stress is reduced, and on the one hand reduces the cooling velocity of postwelding；On the other hand in the welding process, the increase of electrode pressure
The generation that can reduce electric spark and spatter phenomenon improves welding quality, and effectively reduces postwelding crystallization and answer
Power, drawing force further increase, and increase to and realize button fracture compared with copper sheet raising 14% is not added with for 4.34kN.Fig. 4 is pre-
Thermal parameter 8kA, 20cycle, welding current, weld interval, electrode pressure is respectively 16kA, the spot welding under 20cycle, 2.7kN
Joint interface pattern.
2.2.5 coating lanthanum powder is to the influence of aluminium/steel tack-weld mechanical property
The lanthanum powder that purity is greater than or equal to 99%, 200 mesh is coated on copper sheet, and coats the side direction of lanthanum powder
TRIP980 high-strength steel.It is 8kA in pre- thermal parameter, 20cycle, welding current, weld interval, electrode pressure is respectively 16kA,
It is 4.59kN that drawing force, which reaches maximum value, under the conditions of 20cycle, 2.7kN, improves 21% compared with copper sheet is not added with.In copper sheet side
After face coats lanthanum powder, lanthanum powder surface forms lanthana soon, and lanthanum and lanthana can improve TRIP980 high-strength steel side
Thermal stress when crystallization condition and the crystallization of reduction molten bath, to reduce 6061-T6 aluminium alloy side and TRIP980 high-strength steel side
Crystallization condition difference and reduce commissure crackle generation, and lanthana and lanthanum itself also have the function of refinement crystal grain,
The reason of these two aspects, refines weld seam two sides crystal grain uniformly.
2.2.6 the mixed-powder of gadolinium powder and lanthanum powder is coated to the influence of aluminium/steel tack-weld mechanical property
It is coated with the mixed-powder of gadolinium powder and lanthanum powder in pure copper sheet, and coats the side direction of mixed-powder
TRIP980 high-strength steel, gadolinium powder purity are greater than or equal to 99%, 200 mesh, and lanthanum powder purity is greater than or equal to 99%, 200 mesh；
The mass ratio of gadolinium powder and lanthanum powder is 1:7.It is 8kA, 20cycle, welding current, weld interval, electrode in pre- thermal parameter
Pressure is respectively 16kA, and it is 5.42kN that drawing force, which reaches maximum value, under the conditions of 20cycle, 2.7kN, is improved compared with copper sheet is not added with
43%.After the mixed-powder that copper sheet one side coats gadolinium powder and lanthanum powder, lanthanum powder surface forms lanthana soon, lanthanum and
Thermal stress when lanthana can improve the crystallization condition of TRIP980 high-strength steel side and reduce molten bath crystallization, to reduce
The generation of the crystallization condition difference and reduction commissure crackle of 6061-T6 aluminium alloy side and TRIP980 high-strength steel side, and
Lanthana and lanthanum itself also have the function of that the reason of refinement crystal grain, these two aspects refines weld seam two sides crystal grain uniformly；It mixes
Miscellaneous gadolinium powder helps to strengthen the improvement of TRIP980 high-strength steel side crystallization condition and the Grain Refinement Effect of lanthanum and lanthana, from
And drawing force greatly improved.
Summarize: overlap joint copper sheet is 8kA, 20cycle, welding current, weld interval, electrode pressure difference in pre- thermal parameter
It is 4.34kN that for 16kA, under the conditions of 20cycle, 2.7kN, drawing force, which reaches maximum value, improves 14% compared with copper sheet is not added with；It takes
The copper sheet for connecing coating lanthanum powder is 8kA in pre- thermal parameter, and 20cycle, welding current, weld interval, electrode pressure is respectively
It is 4.34kN that drawing force, which reaches maximum value, under the conditions of 16kA, 20cycle, 2.7kN, improves 21% compared with copper sheet is not added with；Overlap joint
The mixed-powder copper sheet of gadolinium powder and lanthanum powder is 8kA, 20cycle, welding current, weld interval, electrode pressure in pre- thermal parameter
Power is respectively 16kA, and it is 4.34kN that drawing force, which reaches maximum value, under the conditions of 20cycle, 2.7kN, is improved compared with copper sheet is not added with
43%.
Obviously, the above embodiments are merely examples for clarifying the description, and does not limit the embodiments.It is right
For those of ordinary skill in the art, can also make on the basis of the above description it is other it is various forms of variation or
It changes.There is no necessity and possibility to exhaust all the enbodiments.And it is extended from this it is obvious variation or
It changes among still in present patent application scope of protection of the claims.
Claims (10)
1.6061-T6 aluminium alloy and the high-strength steel dissimilar alloy resistance spot welding method of TRIP980, which is characterized in that resistance spot welding
Welding condition is as follows: welding current 6.5kA-10.5kA, weld interval 15cyc-60cyc, electrode pressure 1kN-
3.5kN。
2. 6061-T6 aluminium alloy according to claim 1 and the high-strength steel dissimilar alloy resistance spot welding method of TRIP980,
Be characterized in that, the welding condition of resistance spot welding is as follows: welding current 9.5kA, weld interval 35cyc, electrode pressure are
1.5kN。
3.6061-T6 aluminium alloy and the high-strength steel dissimilar alloy resistance spot welding method of TRIP980, which is characterized in that in 6061-T6 aluminium
Pure copper sheet is overlapped between alloy and TRIP980 high-strength steel or surface is coated with the pure copper sheet of lanthanum powder or gadolinium powder and lanthanum powder.
4. 6061-T6 aluminium alloy according to claim 3 and the high-strength steel dissimilar alloy resistance spot welding method of TRIP980,
It is characterized in that, the side that the mixed-powder of lanthanum powder or gadolinium powder and lanthanum powder is coated in pure copper sheet is high-strength towards TRIP980
Steel.
5. 6061-T6 aluminium alloy according to claim 4 and the high-strength steel dissimilar alloy resistance spot welding method of TRIP980,
It is characterized in that, the coated weight of lanthanum powder is the 0.15-0.3% of copper sheet quality；The coating of the mixed-powder of gadolinium powder and lanthanum powder
Amount is the 0.1-0.2% of copper sheet quality, and the mass ratio of gadolinium powder and lanthanum powder is 1:(5-10).
6. according to 6061-T6 aluminium alloy as claimed in claim 3 to 5 and the high-strength steel dissimilar alloy resistance spot welding side TRIP980
Method, which is characterized in that pure copper sheet overlapped length is more than or equal to 30mm, before welding using angle grinder removal 6061-T6 aluminium alloy with
Burr on TRIP980 high-strength steel side, and surface film oxide is removed with sand paper, it is then miscellaneous with dehydrated alcohol and acetone wiping surface
Matter and greasy dirt.
7. according to 6061-T6 aluminium alloy as claimed in claim 3 to 5 and the high-strength steel dissimilar alloy resistance spot welding side TRIP980
Method, which is characterized in that before welding, also butt joint is needed to be preheated；The condition that butt joint is preheated are as follows: pre- thermocurrent
For 6kA-8kA；Preheating time is 10-20cyc.
8. according to 6061-T6 aluminium alloy as claimed in claim 3 to 5 and the high-strength steel dissimilar alloy resistance spot welding side TRIP980
Method, which is characterized in that the welding condition of resistance spot welding is as follows: welding current 15kA-17kA, weld interval 10cyc-
20cyc, electrode pressure 1kN-3.5kN.
9. according to 6061-T6 aluminium alloy as claimed in claim 3 to 5 and the high-strength steel dissimilar alloy resistance spot welding side TRIP980
Method, which is characterized in that the condition that butt joint is preheated are as follows: pre- thermocurrent is 6kA-8kA, preheating time 10-20cyc；
The welding condition of resistance spot welding is as follows: welding current 15kA-17kA, weld interval 10cyc-20cyc, and electrode pressure is
1kN-3.5kN。
10. 6061-T6 aluminium alloy according to claim 9 and the high-strength steel dissimilar alloy resistance spot welding method of TRIP980,
It is characterized in that, the condition that butt joint is preheated are as follows: pre- thermocurrent is 8kA, preheating time 20cyc；The weldering of resistance spot welding
Narrow bars part are as follows: welding current 16kA, weld interval 20cyc, electrode pressure 2.7kN.
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Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN112171036A (en) * | 2020-09-11 | 2021-01-05 | 北京汽车研究总院有限公司 | Welding method |
Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN201409232Y (en) * | 2009-04-03 | 2010-02-17 | 上海汉源特种陶瓷有限公司 | Silicon nitride heating element |
| CN101854749A (en) * | 2009-04-03 | 2010-10-06 | 上海汉源特种陶瓷有限公司 | Silicon nitride heating element and making method thereof |
| CN102909490A (en) * | 2012-11-09 | 2013-02-06 | 高金菊 | Flux-cored wire for welding austenitic stainless steel |
| CN103753005A (en) * | 2013-10-16 | 2014-04-30 | 吉林大学 | High strength steel-aluminum alloy dissimilar metal connecting method |
| CN107081517A (en) * | 2017-06-28 | 2017-08-22 | 合肥工业大学 | A kind of law temperature joining method of TZM and WRe different alloys |
| CN108950508A (en) * | 2018-07-23 | 2018-12-07 | 河北工业大学 | A kind of high strength anti-corrosion aluminium containing middle layer/magnesium different alloys connector and preparation method thereof |
-
2019
- 2019-07-03 CN CN201910594767.4A patent/CN110280880B/en active Active
Patent Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN201409232Y (en) * | 2009-04-03 | 2010-02-17 | 上海汉源特种陶瓷有限公司 | Silicon nitride heating element |
| CN101854749A (en) * | 2009-04-03 | 2010-10-06 | 上海汉源特种陶瓷有限公司 | Silicon nitride heating element and making method thereof |
| CN102909490A (en) * | 2012-11-09 | 2013-02-06 | 高金菊 | Flux-cored wire for welding austenitic stainless steel |
| CN103753005A (en) * | 2013-10-16 | 2014-04-30 | 吉林大学 | High strength steel-aluminum alloy dissimilar metal connecting method |
| CN107081517A (en) * | 2017-06-28 | 2017-08-22 | 合肥工业大学 | A kind of law temperature joining method of TZM and WRe different alloys |
| CN108950508A (en) * | 2018-07-23 | 2018-12-07 | 河北工业大学 | A kind of high strength anti-corrosion aluminium containing middle layer/magnesium different alloys connector and preparation method thereof |
Non-Patent Citations (2)
| Title |
|---|
| 周振丰: "《铸铁焊接冶金与工艺》", 30 October 2001, 机械工业出版社 * |
| 郑纲等: "中间层铜对铝/钢电阻点焊接头性能的影响", 《机械制造文摘—焊接分册》 * |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN112171036A (en) * | 2020-09-11 | 2021-01-05 | 北京汽车研究总院有限公司 | Welding method |
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