CN101850481B - Copper alloy solder wire for fusion welding of thick and big red copper member and preparation method thereof - Google Patents
Copper alloy solder wire for fusion welding of thick and big red copper member and preparation method thereof Download PDFInfo
- Publication number
- CN101850481B CN101850481B CN2010102058916A CN201010205891A CN101850481B CN 101850481 B CN101850481 B CN 101850481B CN 2010102058916 A CN2010102058916 A CN 2010102058916A CN 201010205891 A CN201010205891 A CN 201010205891A CN 101850481 B CN101850481 B CN 101850481B
- Authority
- CN
- China
- Prior art keywords
- welding wire
- copper
- alloy
- red copper
- rare earth
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Expired - Fee Related
Links
- 238000003466 welding Methods 0.000 title claims abstract description 153
- 239000010949 copper Substances 0.000 title claims abstract description 116
- 229910052802 copper Inorganic materials 0.000 title claims abstract description 100
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 title claims abstract description 97
- 229910000881 Cu alloy Inorganic materials 0.000 title claims abstract description 44
- 238000002360 preparation method Methods 0.000 title claims abstract description 20
- 230000004927 fusion Effects 0.000 title abstract description 6
- 229910000679 solder Inorganic materials 0.000 title description 2
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 60
- 239000000956 alloy Substances 0.000 claims abstract description 60
- 238000002844 melting Methods 0.000 claims abstract description 47
- 230000008018 melting Effects 0.000 claims abstract description 46
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 38
- 229910052761 rare earth metal Inorganic materials 0.000 claims abstract description 38
- 229910052718 tin Inorganic materials 0.000 claims abstract description 23
- 229910052749 magnesium Inorganic materials 0.000 claims abstract description 22
- 238000005303 weighing Methods 0.000 claims abstract description 21
- 238000001192 hot extrusion Methods 0.000 claims abstract description 7
- 239000002994 raw material Substances 0.000 claims abstract description 7
- 238000009413 insulation Methods 0.000 claims description 18
- 238000010792 warming Methods 0.000 claims description 18
- 238000005266 casting Methods 0.000 claims description 14
- 229910052746 lanthanum Inorganic materials 0.000 claims description 12
- 238000001816 cooling Methods 0.000 claims description 11
- 229910052684 Cerium Inorganic materials 0.000 claims description 10
- 238000000034 method Methods 0.000 claims description 9
- 239000000203 mixture Substances 0.000 claims description 9
- 238000005554 pickling Methods 0.000 claims description 6
- 239000002893 slag Substances 0.000 claims description 6
- 238000003756 stirring Methods 0.000 claims description 6
- VEXZGXHMUGYJMC-UHFFFAOYSA-N Hydrochloric acid Chemical compound Cl VEXZGXHMUGYJMC-UHFFFAOYSA-N 0.000 claims description 4
- NBIIXXVUZAFLBC-UHFFFAOYSA-N Phosphoric acid Chemical compound OP(O)(O)=O NBIIXXVUZAFLBC-UHFFFAOYSA-N 0.000 claims description 4
- QAOWNCQODCNURD-UHFFFAOYSA-N Sulfuric acid Chemical compound OS(O)(=O)=O QAOWNCQODCNURD-UHFFFAOYSA-N 0.000 claims description 4
- 238000000137 annealing Methods 0.000 claims description 4
- 239000003610 charcoal Substances 0.000 claims description 4
- 210000002615 epidermis Anatomy 0.000 claims description 4
- 230000006698 induction Effects 0.000 claims description 4
- 229910000147 aluminium phosphate Inorganic materials 0.000 claims description 2
- 235000021110 pickles Nutrition 0.000 claims description 2
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 2
- 229910052751 metal Inorganic materials 0.000 abstract description 71
- 239000002184 metal Substances 0.000 abstract description 71
- 238000000641 cold extrusion Methods 0.000 abstract 1
- 239000011777 magnesium Substances 0.000 description 31
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 29
- 239000004411 aluminium Substances 0.000 description 11
- 238000012360 testing method Methods 0.000 description 10
- 230000000694 effects Effects 0.000 description 9
- 238000005275 alloying Methods 0.000 description 7
- 230000005496 eutectics Effects 0.000 description 7
- 229910052760 oxygen Inorganic materials 0.000 description 7
- 210000001519 tissue Anatomy 0.000 description 7
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 6
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 6
- 239000007788 liquid Substances 0.000 description 6
- 239000001301 oxygen Substances 0.000 description 6
- 238000006243 chemical reaction Methods 0.000 description 5
- 238000005336 cracking Methods 0.000 description 5
- 239000013078 crystal Substances 0.000 description 5
- 239000007789 gas Substances 0.000 description 5
- 210000001503 joint Anatomy 0.000 description 5
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 description 4
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 4
- 229910052759 nickel Inorganic materials 0.000 description 4
- 230000008520 organization Effects 0.000 description 4
- 230000003647 oxidation Effects 0.000 description 4
- 238000007254 oxidation reaction Methods 0.000 description 4
- 229910052710 silicon Inorganic materials 0.000 description 4
- 229910000906 Bronze Inorganic materials 0.000 description 3
- 229910000883 Ti6Al4V Inorganic materials 0.000 description 3
- 239000010974 bronze Substances 0.000 description 3
- KUNSUQLRTQLHQQ-UHFFFAOYSA-N copper tin Chemical compound [Cu].[Sn] KUNSUQLRTQLHQQ-UHFFFAOYSA-N 0.000 description 3
- 150000002910 rare earth metals Chemical class 0.000 description 3
- 238000010583 slow cooling Methods 0.000 description 3
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- 229910001060 Gray iron Inorganic materials 0.000 description 2
- 238000003723 Smelting Methods 0.000 description 2
- IUYOGGFTLHZHEG-UHFFFAOYSA-N copper titanium Chemical compound [Ti].[Cu] IUYOGGFTLHZHEG-UHFFFAOYSA-N 0.000 description 2
- 238000002425 crystallisation Methods 0.000 description 2
- 238000005516 engineering process Methods 0.000 description 2
- 239000012467 final product Substances 0.000 description 2
- 229910052748 manganese Inorganic materials 0.000 description 2
- 239000011572 manganese Substances 0.000 description 2
- 239000000463 material Substances 0.000 description 2
- 238000002156 mixing Methods 0.000 description 2
- 239000010936 titanium Substances 0.000 description 2
- 229910052719 titanium Inorganic materials 0.000 description 2
- 229910001369 Brass Inorganic materials 0.000 description 1
- 206010009866 Cold sweat Diseases 0.000 description 1
- 229910000570 Cupronickel Inorganic materials 0.000 description 1
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
- 229910001069 Ti alloy Inorganic materials 0.000 description 1
- 229910008484 TiSi Inorganic materials 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 239000010951 brass Substances 0.000 description 1
- 238000005219 brazing Methods 0.000 description 1
- 238000004364 calculation method Methods 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- YOCUPQPZWBBYIX-UHFFFAOYSA-N copper nickel Chemical compound [Ni].[Cu] YOCUPQPZWBBYIX-UHFFFAOYSA-N 0.000 description 1
- 230000008025 crystallization Effects 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 230000002950 deficient Effects 0.000 description 1
- 238000010891 electric arc Methods 0.000 description 1
- 239000000945 filler Substances 0.000 description 1
- 230000004907 flux Effects 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
- 229910001338 liquidmetal Inorganic materials 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 150000002736 metal compounds Chemical class 0.000 description 1
- 229910052757 nitrogen Inorganic materials 0.000 description 1
- 229910052698 phosphorus Inorganic materials 0.000 description 1
- 239000011148 porous material Substances 0.000 description 1
- 238000012805 post-processing Methods 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 238000007778 shielded metal arc welding Methods 0.000 description 1
- 239000010703 silicon Substances 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
Landscapes
- Arc Welding In General (AREA)
Abstract
一种用于紫铜厚大构件熔化焊的铜合金焊丝及其制备方法，它涉及用于紫铜厚大构件熔化焊的合金焊丝及制备方法。解决现有紫铜厚大构件在熔化焊时，焊接热裂纹严重，导致焊缝金属及接头力学性能差，及采用现有合金焊丝时焊缝导电性及导热性差的问题。焊丝按重量百分比由0.5%~1%的Mg、2%~7%的Al、0.1%~0.5%的稀土元素、0.5%~1%的Sn和余量铜制成。制备方法：称取原料；熔炼MgAlSnRe中间合金；再将中间合金和Cu熔炼得合金焊丝；再均匀化得铸锭；最后经热挤压和冷挤压得焊丝。采用本发明铜合金焊丝经熔化焊对接厚大构件紫铜得的接头无热裂纹，力学性能好，焊缝金属的导电性与导热性要好于现有合金焊丝得到的焊缝金属。The invention discloses a copper alloy welding wire used for fusion welding of red copper thick and large components and a preparation method thereof, and relates to an alloy welding wire used for fusion welding of red copper thick and large components and a preparation method thereof. The invention solves the problems of severe weld thermal cracks during fusion welding of existing red copper thick and large components, resulting in poor mechanical properties of weld metal and joints, and poor electrical conductivity and thermal conductivity of weld seams when the existing alloy welding wire is used. The welding wire is made of 0.5%~1% Mg, 2%~7% Al, 0.1%~0.5% rare earth elements, 0.5%~1% Sn and the balance copper by weight percentage. Preparation method: weighing raw materials; melting MgAlSnRe master alloy; melting the master alloy and Cu to obtain alloy welding wire; homogenizing to obtain ingot; finally hot extrusion and cold extrusion to obtain welding wire. The joint obtained by using the copper alloy welding wire of the invention to butt the red copper of thick and large components has no thermal cracks, good mechanical properties, and the electrical conductivity and thermal conductivity of the weld metal are better than those obtained by the existing alloy welding wire.
Description
Technical field
The present invention relates to a kind of alloy welding wire that is used for the thick big member melting of red copper and preparation method thereof.
Background technology
Adopt common welding method and welding material to red copper thick plate (thickness is greater than 10mm) when welding, not only the molten bath forms difficulty, and in weld seam crystallisation by cooling process, is prone to fire check.The oxidation of mother metal and airborne oxygen were by electric arc ionization when the origin cause of formation of HOT CRACK FOR WELDING P mainly was arc-welding, and oxygen element enters into welding pool inevitably, in process of setting, can form by Cu at the crystal boundary place
2The liquid film that O and Cu form, when solidifying when proceeding to brittle temperature range, liquid film quilt under the effect of shrinkage stress is torn, and finally forms fire check.Shrinkage stress and liquid film are two principal elements that form the red copper HOT CRACK FOR WELDING P.
At present, there are following several kinds to red copper melting filler wire applicatory:
(1) HS201 copper alloy welding wire
To the most widely used a kind of wlding of red copper molten solder, be widely used in gas welding, SMAW, TIG weldering and the MIG weldering, wherein during gas welding, generally adopt HS201 and CJ301 brazing flux to be used.Contain 0.3%Mn and 0.3%Si among the HS201, purpose is to reduce Cu
2O.But from the actual welding effect, the effect of control fire check is unsatisfactory.Therefore engineering reality is controlled fire check through preheating minimizing shrinkage stress, though preheating has reduced shrinkage stress to a certain extent on the one hand, on the other hand, preheating has increased the oxidation tendency of mother metal, thereby has improved the hot cracking tendency of weld seam.Because existing manganese element silicon can't be avoided the oxidation of weld metal fully among the HS201, therefore, when adopting HS201 to weld, if there is tension in weld metal, fire check can't be avoided.
(2) copper titanium combined wire
This invention is primarily aimed at the nitrogen protection TIG welding of red copper.The welding wire of being invented is a core with the HS201 welding wire, is surrounded by the crust of one deck Ti6Al4V alloy outside.The purpose of the Ti6Al4V alloy that is added is to increase wlding to molten bath and weld metal denitrogenation ability, thereby eliminates the welding pore, but still has following problem: because the Ti6Al4V fusing point is high; Fusing makes the molten bath mobile poor, postwelding weld metal uneven components slowly in the molten bath; Be mingled with many; Hardness is high, and fragility is big, poor impact toughness.In addition, HS201 itself also has Sn, Si element, in the molten bath, combines to generate between the CuTiSn ternary metal compound between compound and TiSi binary metal with Ti and Cu element, and weld metal fragility increases, toughness decline.In addition, weld seam resistivity is 1.7 * 10
-7Ω m is 9 times of mother metal T3 red copper; The weld metal thermal conductivity is 106Wm/K, and mother metal is 391 Wm/K, is 1/4 times of weld metal.Weld seam electric conductivity and thermal conductivity can not be taken into account.
(3) corronil welding wire
The corronil welding wire is invented to Nickel-based Alloy Welding, also can be used for the welding of red copper.The throat thickness maximum can reach 30mm.The interpolation of Ni, Mn, Si improves the surface tension of liquid metal in the welding wire, improves the molten bath flowability, and appearance of weld is good, no fire check, and intensity is high, and plasticity is good.But on the other hand, because nickel content reaches 27% in the wlding, the conductance of postwelding corronil weld metal is compared with the conductance of HS201 weld metal and has been descended 10 times, and cost of material improves more than 3 times, thus big limitations the scope of application of this wlding.
(4) albronze welding wire
Present existing albronze welding wire mainly is the aluminium bronze welding wire, like S214 and S215.This type welding wire is mainly used in the welding of aluminium bronze, brass and the built-up welding of aluminum steel and grey cast-iron, and postwelding weld metal intensity is higher.Aluminum bronze bianry alloy eutectic point aluminum content is 8.3 wt%, and eutectic temperature is 1036 ℃, and wherein the content of aluminium is 8.22wt% among the s214, is positioned at aluminum bronze binary phase diagraml Central Asia eutectic phase region; Aluminium content is 8.75wt% among the S215, is positioned at hypereutectic phase region.When adopting these two kinds of welding wires that red copper is carried out melting, in the welding pool solidification and crystallization process by using, can form (alpha+beta) low melting eutectics tissue, increase the hot cracking tendency of red copper at 1036 ℃; And along with the carrying out of cooling, it is that eutectoid reaction takes place that β meets at 565 ℃, generates (α+γ
2) tissue, the appearance of this tissue can make the weld metal embrittlement, and the phenomenon of this embrittlement is called " slow cooling fragility ", has aggravated the hot cracking tendency of red copper weld metal and joint.In addition, adopt S214,, when the S215 welding wire welds red copper, the resistivity of weld metal is respectively 1.197 * 10
-7Ω m and 1.331 * 10
-7Ω m, and red copper resistivity is 1.91 * 10
-8Ω m, the resistivity of weld metal has reached about 7 times of red copper, greatly reduces the electric conductivity of weld seam; The thermal conductivity of weld metal is respectively 84.7 Wm/K and 71.2 Wm/K, is merely 1/4 ~ 1/5 times of mother metal.Postwelding makes the electric conductivity of red copper member and thermal conductivity seriously descend.In sum, though S214, S215 as one type of wlding that is applicable to aluminium bronze, aludip and grey cast-iron welding, and are not suitable for the welding of red copper.
Summary of the invention
The objective of the invention is in order to solve the existing thick big member of red copper when the melting; HOT CRACK FOR WELDING P is serious; Cause welding joint mechanical property poor; And the problem of weld seam electric conductivity and poor thermal conductivity when adopting existing alloy welding wire, the invention provides a kind of copper alloy welding wire that is used for the thick big member melting of red copper and preparation method thereof.
The copper alloy welding wire that the present invention is used for the thick big member melting of red copper is become by 0.5% ~ 1% Mg, 2% ~ 7% Al, 0.1% ~ 0.5% rare earth element, 0.5% ~ 1% Sn and the copper of surplus by weight percentage, and wherein rare earth element is a kind of among Ce, La and the Y or several kinds mixture wherein.
The quality purity of copper is more than 99.9% among the present invention, for example the T3 red copper; Aluminium is fine aluminium, and quality purity is 99.99%; Mg is a pure magnesium, and quality purity is 99.85 ~ 99.95%; Sn is industrial pure tin, and quality purity is 99.0 ~ 99.9%.
The preparation method that the present invention is used for the copper alloy welding wire of the thick big member melting of red copper realizes through following steps: one, take by weighing following raw material by weight percentage: 0.5% ~ 1% Mg, 2% ~ 7% Al, 0.1% ~ 0.5% rare earth element, 0.5% ~ 1% Sn and the copper of surplus, and wherein rare earth element is a kind of among Ce, La and the Y or several kinds mixture wherein; Two, the Mg that step 1 is taken by weighing, Al and Sn put into intermediate frequency furnace, are warming up to 750 ~ 850 ℃, and insulation 10 ~ 20min gets MgAlSn alloy liquation; Cover charcoal at molten surface in the insulating process, continue to be warming up to 1150 ~ 1250 ℃ then, in MgAlSn alloy liquation, add the rare earth element that step 1 takes by weighing again; Insulation 5 ~ 10min after stirring pushs the alloy surface welding slag then aside and pulls cooling out; Get the MgAlSnRe intermediate alloy; Wherein, by the Ar gas shiled, Re represents rare earth element in the intermediate frequency furnace; Three, the MgAlSnRe intermediate alloy that Cu that step 1 is taken by weighing and step 2 obtain is put into vacuum medium frequency induction furnace; Be warming up to 1150 ~ 1250 ℃; Insulation 25 ~ 40min is poured in the mould then, cools off with stove again; Get the CuMgAlSnRe alloy cast ingot, the front mold of wherein casting is at 300 ℃ of following preheating 30 ~ 60min; Four, the CuMgAlSnRe alloy cast ingot that step 3 is obtained is incubated 2.5 ~ 3.5h under 580 ℃ of temperature; Air cooling gets the CuMgAlSnRe alloy cast ingot of homogenising then; At the bottom of then the CuMgAlSnRe alloy cast ingot being removed shrinkage cavity, ingot, car removes epidermis, is processed into Φ 40mm ingot casting; Five, the Φ 40mm ingot casting that step 4 is obtained is heated to 750 ~ 850 ℃ of hot extrusions to Φ 8.0mm line base; Annealing then; After clearing up the surface again, at room temperature, Φ 8.0mm line base is cold drawn to Φ 2.0mm welding wire; With the pickling of Φ 2.0mm welding wire, promptly get the copper alloy welding wire that is used for the thick big member melting of red copper again.
The present invention is directed to large scale red copper member when melting; The problem that HOT CRACK FOR WELDING P is serious adopts interpolation alloying element Mg, Al, rare earth and Sn to prepare copper alloy welding wire, reaches the purpose of effective control HOT CRACK FOR WELDING P; And the mechanical property of raising welding point, improve welding quality.Copper alloy welding wire of the present invention is compared with conventional aluminum bronze welding wire, does not have (alpha+beta) eutectic structure when biggest advantage is welding red copper and generates and (α+γ
2) eutectoid structure separates out, make seam organization more near and mother metal, thereby obtain more to approach the weld metal of red copper character, when reducing high temperature weld seam hot tearing sensitiveness with improve weld seam fragility.And the electric conductivity of weld metal and thermal conductivity are better than copper alloy welding wire on the market.
The Mg that is used for the copper alloy welding wire of the thick big member melting of red copper of the present invention is added in the wlding as deoxidant element.The compatibility of Mg and oxygen is better than Al and Cu in copper alloy welding wire of the present invention, and therefore following reaction at first takes place in liquid molten bath:
, wherein oxygen element (O) generates MgO with the Mg reaction, has suppressed Cu
2The appearance of O, thus the hot cracking tendency of weld seam reduced.MgO floats on face of weld with the form of welding slag.Because when Mg content was higher, butt welded seam electric conductivity influenced to some extent, so Mg content is less, is merely 0.5 ~ 1.0wt%.With oxygen (O) sufficient reacting, it is residual not have the Mg element during room temperature in the weld seam basically in the molten bath, and the butt welded seam metallicity does not have influence.
Al is as alloying element in the copper alloy welding wire of the present invention, and main effect has: (1) suppresses Cu as deoxidier
2The appearance of O, thus control in the red copper welding by (Cu
2O+Cu) HOT CRACK FOR WELDING P that causes of low melting eutectics tissue.In liquid molten bath; According to The thermodynamics calculation results, reaction equation
carries out to the positive reaction direction all the time.Generate product A l
2O
3Have fusing point height, density little, in liquid molten bath the little characteristics of medium viscosity, on float over face of weld and form welding slag, finally discharge weld seam.Al
2O
3Properties of weld does not cause negative effect.(2) improve weld metal intensity.Except with the Al that oxygen (O) combines, remaining Al all is solid-solubilized in the middle of α-Cu matrix, causes the distortion of lattice of Cu crystal grain, plays the effect of solution strengthening.Because Al content in the strict control welding wire does not have (α+γ in the weld metal when making room temperature basically
2) precipitated phase, do not influence the bond strength of α-Cu crystal boundary.Slow cooling fragility appears when having avoided the welding of employing S214 and S215 welding wire.(3) improve the electric conductivity and the thermal conductivity of weld metal and joint.The electric conductivity and the thermal conductivity of aluminium are only second to copper, compare with other alloying elements Ni, Ti, P, Mg, and be irreplaceable alloying element improving aspect weld seam electric conductivity and the thermal conductivity.
The effect of copper alloy welding wire middle rare earth element of the present invention (a kind of among Ce, La and the Y or wherein several kinds mixture) is auxiliary deoxidation and crystal grain thinning; Because Al content is lower in the wlding; No intermetallic compound is separated out, and seam organization mainly is α-Cu tissue of a certain amount of Al of homogeneous structure-solid solution.If do not add rare earth element, in process of setting, α-Cu crystal grain is thicker, and the mechanical property of butt welded seam metal and joint influences to some extent.After adding rare earth element, seam organization obtains refinement, thereby improves the mechanical property of weld metal and joint.
Add Sn in the copper alloy welding wire of the present invention and mainly play and improve the mobile effect in molten bath, because alloy content is lower in the wlding, make alloy melting point higher, therefore in welding, occur the molten bath easily and be clamminess mobile poorly, the phenomenon of incomplete fusion appears in joint easily.Can reduce molten bath viscosity effectively after adding Sn, improve flowability, obtain flawless welding point.
Preparation method of the present invention is at first under different smelting temperatures; Melting obtains the MgAlSnRe intermediate alloy respectively; Overcome because the difference of alloying element fusing point causes the high Metal Melting of fusing point insufficient; And the too high drawback of low-melting metal smelting temperature obtains the CuAlMgSnRe alloy of even tissue again through the even post processing of step 4.
The present invention compared with prior art has following advantage:
1, through the combined deoxidation effect of Mg, Al and rare earth, can effectively improve the problem of molten bath oxidation, thus the appearance of HOT CRACK FOR WELDING P.
2, seam organization is even, and the Al element has been strengthened weld metal.The appearance and the eutectoid structure (α+γ of low melting eutectics tissue (alpha+beta) when having avoided employing aluminium bronze welding wire
2) the slow cooling fragility that causes, improved the mechanical property of weld seam.
3, can realize carrying out the welding of large scale red copper member, need not preheating, reduce labour intensity, increase work efficiency, improve working environment.
4, the good conductivity of joint and weld metal, thermal conductivity are better than other alloy welding wires such as aluminium bronze welding wire, copper-titanium alloy welding wire and copper nickel bare welding filter metal.The resistivity of weld metal of the present invention is 6.61 * 10
-8Ω m has reduced by 1 times during than employing aluminium bronze welding wire, is merely 3.5 times of mother metal red copper.The thermal conductivity of weld metal is 196 Wm/K, improves more than 1 times during than employing aluminium bronze welding wire, can reach 50% of mother metal red copper.
5, adopt copper alloy welding wire of the present invention to adopt the TIG weldering, the standard that welding large scale red copper member can reach is:
3.5 times of weld metal resistivity
1/2 times of weld metal thermal conductivity
Weld metal percentage elongation >=40%
Weld metal hot strength coefficient 110% ~ 115%
Joint percentage elongation >=15%
Weld metal impact flexibility>=155J/cm
2
Just curved >=170 ° of joints
Curved >=170 ° of the joint back of the body.
6, appearance of weld is good, do not have during welding and splash, pore-free, be mingled with, defective such as incomplete fusion.
7, the production cost of welding wire is low, and preparation method is simple.
In sum, the present invention utilizes Mg, and the copper alloy welding wire that heat conduction that Al element deoxidation property preferably and Al are good and electric conductivity obtain guarantees to obtain when weld seam does not have fire check heat conduction and the good welding point of electric conductivity.
The specific embodiment
Technical scheme of the present invention is not limited to the following cited specific embodiment, also comprises the combination in any between each specific embodiment.
The specific embodiment one: the copper alloy welding wire that this embodiment is used for the thick big member melting of red copper is become by 0.5% ~ 1% Mg, 2% ~ 7% Al, 0.1% ~ 0.5% rare earth element, 0.5% ~ 1% Sn and the copper of surplus by weight percentage, and wherein rare earth element is a kind of among Ce, La and the Y or several kinds mixture wherein.
In this embodiment when rare earth element be among Ce, La and the Y during several kinds mixture, get final product than mixing with any.
When melting, the problem that HOT CRACK FOR WELDING P is serious adopts interpolation alloying element Mg, Al, rare earth and Sn to prepare copper alloy welding wire to this embodiment to large scale red copper member; Reach the purpose of effective control HOT CRACK FOR WELDING P; And the mechanical property of raising welding point, improve welding quality, weld metal percentage elongation>=40%; Weld metal hot strength coefficient 110% ~ 115%, weld metal impact flexibility>=155J/cm
2, just curved>=170 ° of joints, curved>=170 ° of the joint back of the body.
Adopt the copper alloy welding wire of this embodiment, the welding point that obtains through the thick big member of melting butt joint red copper does not have fire check, and the resistivity of weld metal is 6.61 * 10
-8Ω m has reduced by 1 times during than employing aluminium bronze welding wire, is merely 3.5 times of mother metal red copper.The thermal conductivity of weld metal is 196 Wm/K, improves more than 1 times during than employing aluminium bronze welding wire, can reach 50% of mother metal red copper.
The specific embodiment two: this embodiment and the specific embodiment one are different is that the quality purity of copper is more than 99.9%; Aluminium is fine aluminium, and quality purity is 99.99%; Mg is a pure magnesium, and quality purity is 99.85 ~ 99.95%; Sn is industrial pure tin, and quality purity is 99.0 ~ 99.9%.Other parameter is identical with the specific embodiment one.
The specific embodiment three: what this embodiment was different with the specific embodiment one or two is that copper is the T3 red copper.Other parameter is identical with the specific embodiment one or two.
The specific embodiment four: this embodiment and the specific embodiment one, two or three are different is that the copper alloy welding wire that is used for the thick big member melting of red copper is become by 0.6% ~ 0.8% Mg, 2.5% ~ 4% Al, 0.15% ~ 0.3% rare earth element, 0.6% ~ 0.9% Sn and the copper of surplus by weight percentage.Other parameter is identical with the specific embodiment one, two or three.
The specific embodiment five: this embodiment and the specific embodiment one, two or three are different is that the copper alloy welding wire that is used for the thick big member melting of red copper is become by 0.7% Mg, 3% Al, 0.2% rare earth element, 0.8% Sn and the copper of surplus by weight percentage.Other parameter is identical with the specific embodiment one, two or three.
The specific embodiment six: this embodiment is like the specific embodiment one described preparation method who is used for the copper alloy welding wire of the thick big member melting of red copper; Realize through following steps: one, take by weighing following raw material by weight percentage: 0.5% ~ 1% Mg, 2% ~ 7% Al, 0.1% ~ 0.5% rare earth element, 0.5% ~ 1% Sn and the copper of surplus, wherein rare earth element is a kind of among Ce, La and the Y or several kinds mixture wherein; Two, the Mg that step 1 is taken by weighing, Al and Sn put into intermediate frequency furnace, are warming up to 750 ~ 850 ℃, and insulation 10 ~ 20min gets MgAlSn alloy liquation; Cover charcoal at molten surface in the insulating process, continue to be warming up to 1150 ~ 1250 ℃ then, in MgAlSn alloy liquation, add the rare earth element that step 1 takes by weighing again; Insulation 5 ~ 10min after stirring pushs the alloy surface welding slag then aside and pulls cooling out; Get the MgAlSnRe intermediate alloy; Wherein, by the Ar gas shiled, Re represents rare earth element in the intermediate frequency furnace; Three, the MgAlSnRe intermediate alloy that Cu that step 1 is taken by weighing and step 2 obtain is put into vacuum medium frequency induction furnace; Be warming up to 1150 ~ 1250 ℃; Insulation 25 ~ 40min is poured in the mould then, cools off with stove again; Get the CuMgAlSnRe alloy cast ingot, the front mold of wherein casting is at 300 ℃ of following preheating 30 ~ 60min; Four, the CuMgAlSnRe alloy cast ingot that step 3 is obtained is incubated 2.5 ~ 3.5h under 580 ℃ of temperature; Air cooling gets the CuMgAlSnRe alloy cast ingot of homogenising then; At the bottom of then the CuMgAlSnRe alloy cast ingot being removed shrinkage cavity, ingot, car removes epidermis, is processed into Φ 40mm ingot casting; Five, the Φ 40mm ingot casting that step 4 is obtained is heated to 750 ~ 850 ℃ of hot extrusions to Φ 8.0mm line base; Annealing then; After clearing up the surface again, at room temperature, Φ 8.0mm line base is cold drawn to Φ 2.0mm welding wire; With the pickling of Φ 2.0mm welding wire, promptly get the copper alloy welding wire that is used for the thick big member melting of red copper again.
In this embodiment step 1 when rare earth element be among Ce, La and the Y during several kinds mixture, get final product than mixing with any.
Preparation method's technology of this embodiment is simple; The copper alloy welding wire that is used for the thick big member melting of red copper that obtains can effectively be controlled the purpose of HOT CRACK FOR WELDING P; And the mechanical property of raising welding point, improve welding quality, weld metal percentage elongation>=40%; Weld metal hot strength coefficient 110% ~ 115%, weld metal impact flexibility>=155J/cm
2, just curved>=170 ° of joints, curved>=170 ° of the joint back of the body.
Adopt the copper alloy welding wire of this embodiment, the welding point that obtains through the thick big member of melting butt joint red copper does not have fire check, and the resistivity of weld metal is 6.61 * 10
-8Ω m has reduced by 1 times during than employing aluminium bronze welding wire, is merely 3.5 times of mother metal red copper.The thermal conductivity of weld metal is 196 Wm/K, improves more than 1 times during than employing aluminium bronze welding wire, can reach 50% of mother metal red copper.
The specific embodiment seven: this embodiment and the specific embodiment six are different is that the quality purity of copper in the step 1 is more than 99.9%; Aluminium is fine aluminium, and quality purity is 99.99%; Mg is a pure magnesium, and quality purity is 99.85 ~ 99.95%; Sn is industrial pure tin, and quality purity is 99.0 ~ 99.9%.Other step and parameter and specific embodiment six phase are together.
The specific embodiment eight: what this embodiment was different with the specific embodiment six or seven is that copper is the T3 red copper.Other parameter is identical with the specific embodiment six or seven.
The specific embodiment nine: what this embodiment and the specific embodiment six, seven or eight were different is to take by weighing following raw material in the step 1 by weight percentage: 0.6% ~ 0.8% Mg, 2.5% ~ 4% Al, 0.15% ~ 0.3% rare earth element, 0.6% ~ 0.9% Sn and the copper of surplus.Other parameter is identical with the specific embodiment six, seven or eight.
The specific embodiment ten: what this embodiment and the specific embodiment six, seven or eight were different is to take by weighing following raw material in the step 1 by weight percentage: 0.7% Mg, 3% Al, 0.2% rare earth element, 0.8% Sn and the copper of surplus.Other parameter is identical with the specific embodiment six, seven or eight.
The specific embodiment 11: what this embodiment was different with one of specific embodiment six to ten is to be warming up to 800 ℃ in the step 2, and insulation 15min gets MgAlSn alloy liquation.Other step and parameter are identical with one of specific embodiment six to ten.
The specific embodiment 12: what this embodiment was different with one of specific embodiment six to 11 is to continue to be warming up to 1200 ℃ in the step 2 then, in MgAlSn alloy liquation, adds the rare earth element that step 1 takes by weighing again, and back insulation 5min stirs.Other step and parameter are identical with the specific embodiment six to 11.
The specific embodiment 13: what this embodiment was different with one of specific embodiment six to 12 is to be warming up to 1200 ℃ in the step 3, insulation 30min.Other step and parameter are identical with one of specific embodiment six to 12.
The specific embodiment 14: what this embodiment was different with one of specific embodiment six to 13 is that the CuMgAlSnRe alloy cast ingot that in the step 4 step 3 is obtained is incubated 2.5 ~ 3.5h under 580 ℃ of temperature.Other step and parameter are identical with one of specific embodiment six to 13.
The CuMgAlSnRe alloy cast ingot is incubated homogenising and handles in this embodiment under 580 ℃ of temperature, makes in the CuMgAlSnRe alloy cast ingot each alloying component more even.
The specific embodiment 15: what this embodiment was different with one of specific embodiment six to 14 is that the Φ 40mm ingot casting that in the step 5 step 4 is obtained is heated to 800 ℃ of hot extrusions to Φ 8.0mm line base.Other step and parameter are identical with one of specific embodiment six to 14.
The specific embodiment 16: this embodiment is different with one of specific embodiment six to 15 be in the step 5 with the pickle of Φ 2.0mm welding wire pickling by mass percentage by 10% sulfuric acid, 10% phosphoric acid, 10% the hydrochloric acid and the water of surplus are formed.Other step and parameter are identical with one of specific embodiment six to 15.
The specific embodiment 17: the preparation method that this embodiment is used for the copper alloy welding wire of the thick big member melting of red copper, realize through following steps: one, take by weighing following raw material by weight percentage: 0.7% Mg, 3% Al, 0.2% rare earth element ce and La (mass ratio of Ce and La is 1:1), 0.8% Sn and the copper of surplus; Two, the Mg that step 1 is taken by weighing, Al and Sn put into intermediate frequency furnace, are warming up to 800 ℃, and insulation 15min gets MgAlSn alloy liquation; Cover charcoal at molten surface in the insulating process, continue to be warming up to 1200 ℃ then, in MgAlSn alloy liquation, add rare earth element ce and the La that step 1 takes by weighing again; Insulation 5min after stirring pushs the alloy surface welding slag then aside and pulls cooling out; Get the MgAlSnRe intermediate alloy; Wherein, by the Ar gas shiled, Re represents rare earth element ce and La in the intermediate frequency furnace; Three, the MgAlSnRe intermediate alloy that Cu that step 1 is taken by weighing and step 2 obtain is put into vacuum medium frequency induction furnace, is warming up to 1200 ℃, insulation 30min; Be poured in the mould then; With the stove cooling, get the CuMgAlSnRe alloy cast ingot again, the front mold of wherein casting is at 300 ℃ of following preheating 30min; Four, the CuMgAlSnRe alloy cast ingot that step 3 is obtained is incubated 3h under 580 ℃ of temperature, air cooling gets the CuMgAlSnRe alloy cast ingot of homogenising then, then the CuMgAlSnRe alloy cast ingot is removed shrinkage cavity, ingot at the bottom of, car removes epidermis, is processed into Φ 40mm ingot casting; Five, the Φ 40mm ingot casting that step 4 is obtained is heated to 800 ℃ of hot extrusions to Φ 8.0mm line base; Annealing then; After clearing up the surface again, at room temperature, Φ 8.0mm line base is cold drawn to Φ 2.0mm welding wire; With the pickling of Φ 2.0mm welding wire, promptly get the copper alloy welding wire that is used for the thick big member melting of red copper again.
Copper is that quality purity is in the T3 red copper more than 99.9% in this embodiment step 1; Aluminium is fine aluminium, and quality purity is 99.99%; Mg is a pure magnesium, and quality purity is 99.85 ~ 99.95%; Sn is industrial pure tin, and quality purity is 99.0 ~ 99.9%.
The welding wire that is used for thick big the not preheating welding of red copper that this embodiment is obtained docks the melting test to the copper plate that is of a size of 250 * 100 * 10mm, gets welding point.
This embodiment is tested welding point as follows: at room temperature carry out the contained HOT CRACK FOR WELDING P test of rigidity and carry out the test of face crack rate and section crack rate; Adopt CSS-44100 type universal testing machine to carry out the mensuration of hot strength and percentage elongation; Adopt impact-toughness tester to carry out the impact flexibility test; And the bending property test, test result is as shown in table 1.
Table 1 performance that to be the welding wire that is used for thick big the not preheating welding of red copper that obtains of the specific embodiment 17 dock the weld metal that melting obtains to copper plate.
Table 1
Visible by table 1, at room temperature carry out face crack and section crack not occurring, no hot cracking tendency after rigidity is restrained the HOT CRACK FOR WELDING P test; And the mechanical property of weld metal is also fine.
The hot strength coefficient of the weld metal that this embodiment obtains reaches 115%, and wherein, the computing formula of tensile strength coefficient is: weld metal intensity/strength of parent * 100%, the hot strength of mother metal T3 red copper is 220MPa.
This embodiment has carried out electric conductivity and thermal conductivity test to the weld metal that obtains, and test result shows that the resistivity of weld metal is 6.61 * 10
-8Ω m, (weld metal resistivity is 1.331 * 10 than adopting the aluminium bronze welding wire
-7) time reduced by 1 times, be merely 3.5 times of mother metal T3 red copper.The thermal conductivity of weld metal is 196 Wm/K, improves more than 1 times during than employing aluminium bronze welding wire (the weld metal thermal conductivity is 71.2 Wm/K), can reach 50% of mother metal red copper.Adopt the electric conductivity and the thermal conductivity of the weld seam that the welding wire of this embodiment obtains good.
Claims (9)
1. copper alloy welding wire that is used for the thick big member melting of red copper; The copper alloy welding wire that it is characterized in that being used for the thick big member melting of red copper is become by 0.5% ~ 1% Mg, 2% ~ 7% Al, 0.1% ~ 0.5% rare earth element, 0.5% ~ 1% Sn and the copper of surplus by weight percentage, and wherein rare earth element is a kind of among Ce, La and the Y or several kinds mixture wherein.
2. a kind of copper alloy welding wire that is used for the thick big member melting of red copper according to claim 1, the copper alloy welding wire that it is characterized in that being used for the thick big member melting of red copper are become by 0.6% ~ 0.8% Mg, 2.5% ~ 4% Al, 0.15% ~ 0.3% rare earth element, 0.6% ~ 0.9% Sn and the copper of surplus by weight percentage.
3. a kind of copper alloy welding wire that is used for the thick big member melting of red copper according to claim 1, the copper alloy welding wire that it is characterized in that being used for the thick big member melting of red copper are become by 0.7% Mg, 3% Al, 0.2% rare earth element, 0.8% Sn and the copper of surplus by weight percentage.
4. a kind of preparation method who is used for the copper alloy welding wire of the thick big member melting of red copper as claimed in claim 1; The preparation method who it is characterized in that being used for the copper alloy welding wire of the thick big member melting of red copper realizes through following steps: one, take by weighing following raw material by weight percentage: 0.5% ~ 1% Mg, 2% ~ 7% Al, 0.1% ~ 0.5% rare earth element, 0.5% ~ 1% Sn and the copper of surplus, and wherein rare earth element is a kind of among Ce, La and the Y or several kinds mixture wherein; Two, the Mg that step 1 is taken by weighing, Al and Sn put into intermediate frequency furnace, are warming up to 750 ~ 850 ℃, and insulation 10 ~ 20min gets MgAlSn alloy liquation; Cover charcoal at molten surface in the insulating process, continue to be warming up to 1150 ~ 1250 ℃ then, in MgAlSn alloy liquation, add the rare earth element that step 1 takes by weighing again; Insulation 5 ~ 10min after stirring pushs the alloy surface welding slag then aside and pulls cooling out; Get the MgAlSnRe intermediate alloy; Wherein, by the Ar gas shiled, Re represents rare earth element in the intermediate frequency furnace; Three, the MgAlSnRe intermediate alloy that Cu that step 1 is taken by weighing and step 2 obtain is put into vacuum medium frequency induction furnace; Be warming up to 1150 ~ 1250 ℃; Insulation 25 ~ 40min is poured in the mould then, cools off with stove again; Get the CuMgAlSnRe alloy cast ingot, the front mold of wherein casting is at 300 ℃ of following preheating 30 ~ 60min; Four, the CuMgAlSnRe alloy cast ingot that step 3 is obtained is incubated 2.5 ~ 3.5h under 580 ℃ of temperature; Air cooling gets the CuMgAlSnRe alloy cast ingot of homogenising then; At the bottom of then the CuMgAlSnRe alloy cast ingot being removed shrinkage cavity, ingot, car removes epidermis, is processed into Φ 40mm ingot casting; Five, the Φ 40mm ingot casting that step 4 is obtained is heated to 750 ~ 850 ℃ of hot extrusions to Φ 8.0mm line base; Annealing then; After clearing up the surface again, at room temperature, Φ 8.0mm line base is cold drawn to Φ 2.0mm welding wire; With the pickling of Φ 2.0mm welding wire, promptly get the copper alloy welding wire that is used for the thick big member melting of red copper again.
5. a kind of preparation method who is used for the copper alloy welding wire of the thick big member melting of red copper according to claim 4 is characterized in that being warming up in the step 2 800 ℃, and insulation 15min gets MgAlSn alloy liquation.
6. according to claim 4 or 5 described a kind of preparation methods that are used for the copper alloy welding wire of the thick big member melting of red copper; It is characterized in that continuing to be warming up to 1200 ℃ in the step 2 then; In MgAlSn alloy liquation, add the rare earth element that step 1 takes by weighing again, back insulation 5min stirs.
7. a kind of preparation method who is used for the copper alloy welding wire of the thick big member melting of red copper according to claim 6 is characterized in that being warming up in the step 3 1200 ℃, insulation 30min.
8. according to the described a kind of preparation method who is used for the copper alloy welding wire of the thick big member melting of red copper of step 4, it is characterized in that the Φ 40mm ingot casting that in the step 5 step 4 is obtained is heated to 800 ℃ of hot extrusions to Φ 8.0mm line base.
9. according to claim 4,5,7 or 8 described a kind of preparation methods that are used for the copper alloy welding wire of the thick big member melting of red copper; It is characterized in that in the step 5 the pickle of Φ 2.0mm welding wire pickling by mass percentage by 10% sulfuric acid; 10% phosphoric acid, 10% the hydrochloric acid and the water of surplus are formed.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN2010102058916A CN101850481B (en) | 2010-06-22 | 2010-06-22 | Copper alloy solder wire for fusion welding of thick and big red copper member and preparation method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN2010102058916A CN101850481B (en) | 2010-06-22 | 2010-06-22 | Copper alloy solder wire for fusion welding of thick and big red copper member and preparation method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN101850481A CN101850481A (en) | 2010-10-06 |
| CN101850481B true CN101850481B (en) | 2012-03-07 |
Family
ID=42802247
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN2010102058916A Expired - Fee Related CN101850481B (en) | 2010-06-22 | 2010-06-22 | Copper alloy solder wire for fusion welding of thick and big red copper member and preparation method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN101850481B (en) |
Families Citing this family (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102079019A (en) * | 2011-01-19 | 2011-06-01 | 浙江银宇焊接新材料科技有限公司 | Multi-element compounded micro-alloyed Al-Mg-Sc series welding wire and preparation method thereof |
| CN102581509A (en) * | 2012-03-27 | 2012-07-18 | 郑州机械研究所 | Mg-Al-Cu-Sn magnesium alloy soldering solder |
| CN112570993B (en) * | 2020-12-04 | 2024-01-30 | 无锡通伟电力设备有限公司 | Processing method of conductive copper bus |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1557604A (en) * | 2004-01-19 | 2004-12-29 | 解明远 | High strength copper alloy welding wire and its use |
| RU2265674C1 (en) * | 2004-08-09 | 2005-12-10 | Федеральное государственное унитарное предприятие "Всероссийский научно-исследовательский институт авиационных материалов" (ФГУП "ВИАМ") | Composition of welding wire |
| CN101518859A (en) * | 2009-03-23 | 2009-09-02 | 天津市金龙焊接材料有限公司 | High strength corrosion-resistant brazing copper alloy welding wire |
Family Cites Families (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6120693A (en) * | 1984-07-06 | 1986-01-29 | Toshiba Corp | Bonding wire |
| JPS6137396A (en) * | 1984-07-31 | 1986-02-22 | Isuzu Motors Ltd | Copper alloy welding rod |
| US20040115089A1 (en) * | 1999-07-02 | 2004-06-17 | Berkenhoff Gmbh. | Weld-solder filler |
-
2010
- 2010-06-22 CN CN2010102058916A patent/CN101850481B/en not_active Expired - Fee Related
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1557604A (en) * | 2004-01-19 | 2004-12-29 | 解明远 | High strength copper alloy welding wire and its use |
| RU2265674C1 (en) * | 2004-08-09 | 2005-12-10 | Федеральное государственное унитарное предприятие "Всероссийский научно-исследовательский институт авиационных материалов" (ФГУП "ВИАМ") | Composition of welding wire |
| CN101518859A (en) * | 2009-03-23 | 2009-09-02 | 天津市金龙焊接材料有限公司 | High strength corrosion-resistant brazing copper alloy welding wire |
Non-Patent Citations (2)
| Title |
|---|
| JP昭61-20693A 1986.01.29 |
| JP昭61-37396A 1986.02.22 |
Also Published As
| Publication number | Publication date |
|---|---|
| CN101850481A (en) | 2010-10-06 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN101941122B (en) | Welding wire matched with corrosion-resistant aluminum-magnesium-scandium alloy and preparation method thereof | |
| CN101380703B (en) | Multiple microalloying scandium-containing hydronalium welding wire and preparation method thereof | |
| CN101716704B (en) | Al-Mg-Er welding wire and preparation process thereof | |
| CN102943193B (en) | Grain refinement machining process of hard aluminium alloy cast ingot | |
| CN103273214B (en) | A kind of high-strength aluminium zinc-magnesium scandium alloy welding wire and preparation method thereof | |
| CN104722945A (en) | Ultra-fine grain aluminum alloy gold welding wire and preparation method thereof | |
| CN104959748A (en) | Flux-cored wire special for maritime work low-temperature high-strength steel | |
| CN112975203B (en) | Al-Si-Cu-Ni brazing filler metal for connecting Cu/Al joint and preparation method thereof | |
| CN105385906B (en) | A kind of Al Mg In series solder wires and preparation method thereof | |
| CN101323060A (en) | A kind of magnesium alloy medium temperature brazing material | |
| CN100361777C (en) | A kind of high-strength low thermal cracking aluminum-copper alloy welding wire and its preparation method and application | |
| CN109128572B (en) | Welding wire for aluminum-copper alloy and preparation method and application thereof | |
| CN102079019A (en) | Multi-element compounded micro-alloyed Al-Mg-Sc series welding wire and preparation method thereof | |
| CN101623800B (en) | Magnesium-based brazing filler metal alloy and preparation method thereof | |
| CN104785950B (en) | A kind of Laser Welding of Aluminum Alloys Al Mg Sc series solder wires | |
| CN107779702A (en) | A kind of 7XXX high strength alumin ium alloy special welding wires containing Ag and Sc | |
| JPS63206445A (en) | Aluminum-lithium ternary alloy | |
| CN112481527A (en) | 6XXX series aluminum alloy round ingot and preparation method thereof | |
| CN101850481B (en) | Copper alloy solder wire for fusion welding of thick and big red copper member and preparation method thereof | |
| CN102862002A (en) | Al-Si-Zn-Ge low-melting-point aluminum-based brazing filler metal and preparation method thereof | |
| CN106862796A (en) | A kind of aluminium copper earthing material welding wire and preparation method thereof | |
| CN113897519A (en) | Al-Mn-Mg-Si-Ti-Sn casting alloy for realizing vacuum brazing by vacuum die casting and preparation method thereof | |
| CN109434319A (en) | TIG (tungsten inert gas) welding wire for aluminum alloy and preparation method thereof | |
| CN114589430B (en) | A kind of Al-Mg alloy welding wire and preparation method thereof | |
| US4108688A (en) | Cast aluminum plate and method therefor |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| C14 | Grant of patent or utility model | ||
| GR01 | Patent grant | ||
| CF01 | Termination of patent right due to non-payment of annual fee |
Granted publication date: 20120307 Termination date: 20160622 |
|
| CF01 | Termination of patent right due to non-payment of annual fee |