CN1990160A - Baked flux cored wire for gas shield arc welding having excellent rust resistance and feedability and a method for preparing thereof - Google Patents
Baked flux cored wire for gas shield arc welding having excellent rust resistance and feedability and a method for preparing thereof Download PDFInfo
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- CN1990160A CN1990160A CNA200610144881XA CN200610144881A CN1990160A CN 1990160 A CN1990160 A CN 1990160A CN A200610144881X A CNA200610144881X A CN A200610144881XA CN 200610144881 A CN200610144881 A CN 200610144881A CN 1990160 A CN1990160 A CN 1990160A
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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
- B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
- B23K35/02—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by mechanical features, e.g. shape
- B23K35/0255—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by mechanical features, e.g. shape for use in welding
- B23K35/0261—Rods, electrodes, wires
-
- 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
- B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
- B23K35/02—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by mechanical features, e.g. shape
- B23K35/0255—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by mechanical features, e.g. shape for use in welding
- B23K35/0261—Rods, electrodes, wires
- B23K35/0266—Rods, electrodes, wires flux-cored
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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
- B23K9/00—Arc welding or cutting
- B23K9/16—Arc welding or cutting making use of shielding gas
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C2204/00—End product comprising different layers, coatings or parts of cermet
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Abstract
The invention relates to a baked flux cored wire for automatic or automatic-manual gas shield arc welding and a method for preparing thereof. The surface of the baked flux cored wire of the invention is composed of flat working surface, concavo convex surface and concave formed along surface circumference direction and relative to the working surface as negative direction to form mixing surface, in which, oxide film thickness of the flat working surface is in the range of 0.10-0.90 mu m, the ratio (dr/di) of the fact arc length of circular arc (dr) to the showing length of circular arc (di) is in the range of 1.015-1.615. The invention makes the oxide film on the soldering wire surface with good thinness, further obtaining the oxide film with high content of Fe3O4 having good rust resistance. When using flux cored wire with good rust resistance, the contact between the conducting nozzle and the flux cored wire is stable, with good sending wire performance, the ratio of Fe3O4 with good rust resistance is high, even placing for a long time, without rustiness.
Description
Technical field
The present invention relates to a kind of sintering flux-cored wire and manufacture method thereof that is used for automatic or semi-automatic gas shielded arc welding; sintering (baked) flux-cored wire that is used for gas shielded arc welding of the present invention is handled through oversintering (baking); resistance to rust (rust resistance) is good; even long-time welding can not got rusty yet; the bonding force of sinter layer is powerful, has improved wire feeding property.
Background technology
The aforementioned manufacture method that is used for the sintering flux-cored wire of gas shielded arc welding comprises following operation: the band steel after reducing is bent to filling solder flux behind the U font; drawing is carried out sintering processes after being processed into certain size, and the welding wire surface of crossing in sintering processes for the wire feeding property that improves when welding welding wire applies and comprises oil, wax, MoS
2And the surface conditioning agent of thing such as graphite.
Use drawing compound for drawing successfully in drawing process, drawing compound also can remain on the welding wire after certain size was processed in drawing.In order to eliminate the organic substance in the drawing compound that remains in after the drawing on the welding wire surface and carry out sintering processes.If unclear organic matter removal matter and directly welding will increase the weld defect of worm channel (warm hole) and so on and the quantity of diffusivity hydrogen, and then the molten attached metal rerum natura after the welding caused have a strong impact on.
Can take two kinds of sintering processing methods this moment, carries out sintering and generate the method for oxide-film and carry out sintering and do not generate the method for oxide-film in the reduction atmosphere in the oxidation atmosphere.
Wherein, the sintering atmosphere being controlled at reduction carries out spy that the conventional art of sintering processes can Japan after the atmosphere and opens flat 04-081297 number and be example.Preceding method is because needs add elements such as hydrogen or nitrogen artificially in the sintering atmosphere, so its production cost is higher relatively.
The sintering atmosphere is controlled at the technology of the laggard capable sintering processes of oxidation atmosphere, at first make atmosphere oxygen and organic substance burning back in the sintering furnace generate oxygen, make it then and be with the steel crust to react and generate oxide-film, therefore the generation result of aforementioned oxide-film can be different with atmosphere gas along with temperature.
That is to say, belong to high-temperature oxydation temperature is carried out more than 570 ℃ the time can generate FeO, Fe
2O
3, Fe
3O
4Phase can generate Fe when 570 ℃ of following temperature that belong to low-temperature oxidation are carried out
2O
3, Fe
3O
4Phase.
The sintering circuit of flux-cored wire is carried out in the scope of 300 ℃～570 ℃ of general organic substance decomposition temperatures usually.If sintering temperature is too high, the solder flux metal dust that is filled in flux-cored wire inside is oxidized and can't melt attached when welding or the performance deoxidation.
When oxidation, generate mutually in, Fe
3O
4Resistance to rust be better than Fe
2O
3, therefore just need to improve the Fe of oxide-film in order to make the good flux-cored wire of resistance to rust
3O
4Ratio.But the Fe that forms oxide-film
2O
3With Fe
3O
4Be the very high insulator of resistance, so oxide-film the time stoped the energising of copper ignition tip (contact tip) to welding wire in welding, made that the welding wire fusion is irregular, the electric arc instability increases splashing amount and causes the unstable phenomenon of wire feeding property.If oxide-film is fine and closely woven inadequately, ignition tip is inner can to come off fine oxide-film composition because of the friction between welding wire and the ignition tip, and the fine oxide-film composition that comes off will be accumulated in the phenomenon that ignition tip is inner and cause ignition tip to block.
Therefore in order to make the good sintering flux-cored wire that is used for gas shielded arc welding of wire feeding property and resistance to rust, need to generate Fe
3O
4Higher, the fine and closely woven ultra-thin oxide-film of content.
About can give an example No. the 1460964th, BP of the conventional art of aforementioned oxide-film.
After the solid welding wire manufacture method of aforementioned techniques is carried out drawing procedure at the metallic rod that does not have the filling solder flux (Rod), drawing compound is carried out the wet type degreasing, to apply operation in order preventing to get rusty then, to it is characterized by: substituted the mode of production that applies Cu, Zn and Ag to generate thin oxide-film.
The aforementioned conventional technology be characterized as fine and closely woven ultra-thin oxide-film, this point is of the same mind with the inventor's.But solid welding wire and flux-cored wire have the difference of essence on manufacturing technology, for example, solid welding wire carries out drawing processing at metallic rod, flux-cored wire then carries out drawing processing behind band steel inner filling solder flux, not only on drawing mechanism, differ greatly, and it is also different when removing drawing compound after the drawing procedure, solid welding wire can take wet type to remove method, when yet flux-cored wire takes wet type removing method to remove drawing compound, moisture will immerse seam (Joint) inside of flux-cored wire and make the solder flux moisture absorption, in when welding molten attached metal is caused significant impact, therefore do not take wet processed and carry out sintering processes.Therefore conventional art has very large different on product, sintering circuit and drawing procedure with the present invention.
Spy that can Japan about the conventional art of sintering flux-cored wire opens institute and is example 57-127597 number, according to the explanation of aforementioned patent, and CO
2Content reaches 70% when above, just can obtain the good fine and closely woven ultra-thin oxide-film of wire feeding property and resistance to rust in 3 hours 250 ℃ of temperature sintering processes with 550 ℃.
The fine and closely woven ultra-thin oxide-film of aforementioned invention has good resistance to rust and wire feeding property, but except sintering processes atmosphere, temperature and time, the surface roughness of welding wire also can cause bigger influence to the characteristic of oxide-film.That is to say, carry out drawing procedure after, the drawing welding wire will comprise the finished surface that generates by the friction between drawing die and the band steel crust, and not possess the convex-concave surface of the finished surface that is generated by drawing compound.Wherein, the specific area of convex-concave surface is greater than finished surface, and area that can catalytic oxidation atmosphere gas is also bigger, and the growth rate of oxide-film is also fast than finished surface.Therefore finished surface and convex-concave surface become and cause the uneven factor of oxide-film, and resistance to rust and wire feeding property are caused bigger influence.When using the welding wire with more convex-concave surface to generate that its wire feeding property of test is with resistance to rust behind the oxide-film according to the aforementioned conventional technology, discovery does not generate fine and closely woven ultra-thin oxide-film.
And, if the growth of oxide-film is controlled at below the certain thickness, so just do not need CO
2Atmosphere reaches more than 70%, also can obtain fine and closely woven oxide-film under general air atmosphere.Generally speaking, in order to obtain fine and closely woven oxide-film, oxide thickness can be controlled at that certain numerical value is following, what characteristic the welding wire surface after the drawing has is most important two keys.
Summary of the invention
In order to solve the aforesaid drawbacks of conventional art; the purpose of this invention is to provide a kind of sintering flux-cored wire that is used for gas shielded arc welding; the present invention limits the surface roughness and the oxide thickness of welding wire within the specific limits; generate evenly fine and closely woven oxide-film; can be during welding at the fine oxide-film of ignition tip inner accumulation, wire feeding property and resistance to rust are good.
The invention provides a kind of sintering flux-cored wire that is used for gas shielded arc welding; the present invention has good wire feeding property and resistance to rust; the surface of the flux-cored wire of handling through oversintering (Baking) is by smooth finished surface; convex-concave surface and with respect to finished surface be negative direction (towards the welding wire center) and surfacewise the depression that forms of circumferencial direction formed blending surface; the oxide thickness of aforementioned smooth finished surface is in 0.10～0.90 mu m range, and the actual arc length of circular arc (dr) is in the ratio (dr/di) of circular arc performance length (di) in 1.015～1.615 the scope.
The aforementioned oxide-film of the sintering flux-cored wire that is used for gas shielded arc welding of the present invention is by Fe
2O
3Phase and Fe
3O
4Phase composition.
The present invention is used for gas shielded arc welding and has the manufacture method of the sintering flux-cored wire of good wire feeding property and resistance to rust; band steel crust is carried out tubulation; the filling solder flux; drawing; sintering and surface conditioning agent apply operation and make; it is characterized by: the surface roughness of aforementioned band steel crust is as the criterion with the Ra value and is controlled in the scope of 0.20～1.43 μ m; the drawing speed of aforementioned tubulation operation is controlled in the scope of 20～150m/min; the second stage drawing speed then is controlled in the scope of 100～1800m/min, carries out aforementioned sintering circuit 20 minutes to 12 hours in 300～570 ℃ of temperature ranges under the general atmosphere atmosphere.
As previously mentioned, when carrying out sintering processes the surface roughness of welding wire and oxide thickness are controlled in the particular range, have improved the Fe of resistance to rust excellence
3O
4Phase ratio, the deviation of each position of welding wire (finished surface, concavo-convex and sunk surface) is less, and the oxide-film of generation is thinner and fine and closely woven, can be at the fine oxide-film of ignition tip inner accumulation when therefore welding.
The sintering flux-cored wire that is used for gas shielded arc welding provided by the invention, its resistance to rust and wire feeding property are better than traditional sintering flux-cored wire that is used for gas shielded arc welding.
Description of drawings
Fig. 1 is the SEM microphoto that only has the welding wire surface of finished surface,
Fig. 2 is the SEM microphoto that does not have the welding wire surface of finished surface,
Fig. 3 is to have finished surface and is the welding wire surface SEM microphoto on the surface, surface of negative direction (towards the welding wire center) depression with respect to finished surface,
Only there is formed oxide-film SEM microphoto on the welding wire surface of finished surface in Fig. 4,
There is not formed oxide-film SEM microphoto on the welding wire surface of finished surface in Fig. 5,
Front and back SEM microphoto when Fig. 6 and Fig. 7 are to use aforementioned video analytic system to measure the actual arc length of circular arc,
Fig. 8 is that employed chord length is measured the SEM microphoto of using image when utilizing video analytic system to calculate circular arc performance length (di),
Fig. 9 is the curve map of relation between chord length (l), welding wire radius (r), circle interior angle (θ) and the circular arc performance length (di).
Figure 10 is the XRD facies analysis figure that carries out the oxide-film that generates after the sintering processes in the temperature below 570 ℃,
Figure 11 is the oxide-film optical microscope photograph under the various sintering conditions, and the sintering condition of Figure 11 a is that carry out sintering processes under 300 ℃ 1 hour 30 minutes, the sintering condition of Figure 11 b are to carry out sintering processes under 500 ℃ 3 hours, the sintering condition of Figure 11 c are to carry out sintering processes under 650 ℃ 1 hour.
The specific embodiment
The welding wire surface of flux-cored wire after by drawing be a kind ofly comprised the irregular surface (concavo-convex) that only there is the flat surfaces of finished surface, do not have finished surface, be negative direction (towards the welding wire center) and the mixed type surface that forms depression along circumferencial direction with respect to finished surface.
Finished surface refers to, and uses SEM to amplify 1000 times when becoming 90 ° of directions to observe the welding wire cross sectional image with respect to welding wire length, the planar section that forms along circumferencial direction at welding wire surface by the processing processing of drawing die during drawing.Fig. 1 has shown the SEM microphoto of the planar section, irregular surface and the depressed part that only have aforementioned finished surface respectively to Fig. 3.
As previously mentioned, the specific area of convex-concave surface is higher than finished surface, and the growth rate of oxide-film is than piece, and Fig. 4 and Fig. 5 have shown the oxide-film of oxide-film when not having finished surface when only finished surface being arranged, and oxide thickness is different along with surface roughness.
The increase of specific area can be accelerated the growth rate of oxide-film, and it is big that the oxide thickness difference of finished surface and irregular surface also can become.The ratio of irregular surface is high more, and the inhomogeneities of oxide-film is also high more, and the fine and closely woven property of film is poor more, and then has reduced wire feeding property and resistance to rust.
Owing to the thickness of the oxide-film of irregular surface has reduced fine and closely woven property greater than the thickness of working position, fine oxide-film composition will be accumulated in the phenomenon that ignition tip is inner and cause ignition tip to block during welding.Because there is not finished surface in irregular surface, can't between ignition tip and welding wire, keep stable contacting, will cause bigger frictional force in wire feed conduit (feeding cable) inside during welding and increase the feeding load, and then reduce wire feeding property.
The result of study that the process inventor carries out at the growth relation of surface configuration and oxide-film, when the actual arc length of circular arc (dr) to the ratio (dr/di) of circular arc performance length (di) during in 1.015～1.615 scopes, can obtain the less oxide-film of deviation between each position of welding wire, its wire feeding property excellence.
The actual arc length of circular arc refers to, amplify 1000 times becoming to utilize on 90 ° the cross section SEM with respect to the welding wire length direction, the actual arc length of the circular arc that is equivalent to measurement zone (that is to say depression girth at position and closing of finished surface length on the welding wire surface) of using video analytic system to measure then; Circular arc performance length refers to, use the welding wire actual diameter and the earlier figures picture that calculates by theory in be equivalent to the arc length of measurement zone.
The actual arc length of circular arc (dr) asks method as follows to the ratio (dr/di) of circular arc performance length (di).
At first use video analytic system (Image Analyzing System/Image-Pro Plus 4.5, MediaCybernetics) the actual arc length of circular arc (dr) of measurement welding wire under 1000 multiplying powers.At this moment, the circular arc actual arc length that calculates of video analytic system is equivalent to the length that concavo-convex girth with the depression position on the welding wire surface adds finished surface.
Front and back image when Fig. 6 and Fig. 7 are to use aforementioned video analytic system to measure the actual arc length of circular arc.
Then, use video analytic system under the situation of 1000 multiplying powers, to measure the chord length (l) of welding wire in order to calculate circular arc performance length (di).Fig. 8 is its image.
After trying to achieve chord length (l), as shown in Figure 9, the interior angle that can use trigonometric function to calculate welding wire radius (r) and chord length (l) to be constituted (θ: radian value), try to achieve aforementioned interior angle value after, circular arc performance length (di) is tried to achieve in the multiplying of radius (r) the x circle interior angle (θ) by welding wire again.As long as after therefore measuring the actual diameter of welding wire and draw radius (r) value, can calculate circular arc performance length (di).In order to make the dr/di measured value have objectivity, we get its mean value after having measured any 4 faces.
If the actual arc length of the circular arc that calculates (dr) is lower than 1.015 to the ratio (dr/di) of circular arc performance length (di), to reduce the maintenance energy that sticks to the feeding lubricant on the welding wire surface in order to improve the wire feeding property after the sintering processes, and then reduce the wire feeding property of welding wire; If its value was above 1.615 o'clock, friction resistance during welding wire feeding between ignition tip and the wire feed conduit will increase, wire feeding property is caused harmful effect, and the characteristic deviation between the welding wire surface oxide-film position is bigger, and then makes fine and closely woven property, wire feeding property and the resistance to rust of oxide-film bad.
The inventor has carried out a lot of experiments for surface roughness factor dr/di value is maintained in 1.015～1.615 the scope, and experimental result shows need satisfy following condition.
Bending to behind the U font before the filling solder flux, at first needing the roughness of band steel crust is controlled in the scope of 0.20～1.43 μ m (being as the criterion with the Ra value).
If the roughness of aforementioned band steel crust surpasses 1.43 μ m, even properly controlled follow-up operations such as tubulation, tubulation drawing and second stage drawing, the finish surface of back welding wire of drawing is still too coarse and make the dr/di value exceed limited range of the present invention; If be lower than 0.20 μ m, drawing compound during with the drawing of reduction tubulation is kept ability, after entering tubulation drawing and second stage drawing procedure, the friction stree between drawing die and the band steel crust will significantly increase and cause welding wire to fracture and make the dr/di value exceed 1.615.
And the second stage drawing procedure that need properly regulate tubulation drawing procedure and tubulation drawing.
In order to obtain dr/di value preferably, the tubulation drawing speed behind the tubulation should maintain 20 in the scope of 150m/min.If surpass 150m/min, to when being configured as the band steel of U word or zero font by the tubulation running roller, cause the non-uniform phenomenon of belt steel surface roughness, make the solder flux space of packwall steel inside equably, cause the space deviation at each position, aforesaid belt steel surface roughness is inhomogeneous and each space, position bias phenomenon will make drawing die in the second stage drawing procedure and be with the friction stree between the steel crust to convey to welding wire unevenly and cause convex-concave surface.
Even properly controlled the tubulation drawing procedure, the filling solder flux evenly distributes band steel internal voids, also can't avoid residual a part of space deviation, and aforementioned deviation will reduce in the second stage drawing procedure gradually.Yet the second stage drawing speed is fast more, and the influence that surface roughness is subjected to is also and then big more, so we need control the drawing speed of second stage.
Aforementioned second stage drawing speed should maintain in the scope of 100～1800m/min, when surpassing 1800m/min, the effect that has stoped the space difference of band steel inside to tail off owing to the minimizing of welding wire area, make the friction stree between drawing die and the band steel crust convey to welding wire unevenly and cause convex-concave surface, the surface roughness of welding wire is caused adverse effect.
The tubulation drawing speed is lower than 20m/min, and the second stage drawing speed is when being lower than 100m/min, and not only the dr/di value will be lower than 1.015, and the lubricant that has weakened when carrying out surface treatment procedure after the sintering processes keeps ability, and then has reduced wire feeding property.
Only exist the oxide thickness of the flat surfaces of finished surface should maintain in the scope of 0.10～0.90 μ m, when its thickness is lower than 0.10 μ m, can't remove the organic substance of drawing compound fully, rerum natura to weld metal causes harmful effect, oxide-film can't be evenly distributed on the welding wire surface, a part does not then form oxide-film on the surface, and then has reduced resistance to rust; When surpassing 0.90 μ m, the expansion effects of volume the fine and closely woven property of oxide-film, cause wire feeding property and resistance to rust bad.
＜embodiment 〉
Describe the preferred embodiment of the invention in detail below with reference to accompanying drawing.
Embodiment 1
Present embodiment has shown the dependency relation between roughness, tubulation drawing speed, second stage drawing speed and the surface roughness of being with the steel crust, and table 1 has shown its numerical value.
[table 1]
| NO. | The roughness (μ m) of band steel | Tubulation drawing speed (m/min) | Second stage drawing speed (m/min) | dr/di |
| 1 | 0.85 | 60 | 600 | 1.204 |
| 2 | 1.43 | 150 | 1800 | 1.615 |
| 3 | 1.52 | 120 | 1500 | 1.689 |
| 4 | 1.43 | 20 | 1800 | 1.454 |
| 5 | 1.43 | 20 | 100 | 1.143 |
| 6 | 1.31 | 180 | 1200 | 1.721 |
| 7 | 1.43 | 150 | 100 | 1.274 |
| 8 | 0.20 | 150 | 1800 | 1.454 |
| 9 | 0.20 | 150 | 100 | 1.364 |
| 10 | 0.14 | 80 | 1400 | 1.706 |
| 11 | 0.20 | 80 | 1800 | 1.376 |
| 12 | 1.07 | 120 | 2100 | 1.732 |
| 13 | 0.20 | 20 | 100 | 1.015 |
| 14 | 0.20 | 15 | 90 | 1.010 |
As above shown in the table, the surface roughness of band steel in 0.20 μ m～1.43 mu m ranges, the tubulation drawing speed is in 20m/min～150m/min scope or second stage drawing speed (Nos.1 in 100m/min～1800m/min scope the time, 2,4,5,7,8,9,11,13), the dr/di value is limited at 1.015～1.615 scope.The surface roughness of band steel is big more, and the tubulation drawing speed is fast more, and the second stage drawing speed is got over piece, and the dr/di value is just more near 1.615; The surface roughness of band steel is low more, the tubulation drawing speed is slow more or the second stage drawing speed is slow more, and the dr/di value is just more near 1.015.
As long as each in surface roughness, tubulation drawing speed and the second stage drawing speed of band steel can not limited range according to the invention, the dr/di value will exceed limited range of the present invention.In last table, the No.3 that the belt steel surface roughness is ineligible and 10, ineligible No.6 and the ineligible No.12 and 14 of second stage drawing speed of tubulation drawing speed have illustrated this argument well.
Embodiment 2
Present embodiment has shown oxide-film shape and the characteristic under the various sintering circuit conditions.
It is 1.015～1.615 welding wire (Nos.1 that the inventor uses aforementioned surfaces rugosity factor dr/di value, 2,4,5,7,8,9,11,13) adjust temperature and time and carried out sintering processes in the atmospheric atmosphere below 570 ℃, use XRD to carry out the facies analysis of oxide-film then, its result as shown in figure 10.
The XRD of facies analysis has used the X ' Pert model of Philips company, and measuring condition has been taked the OmegaScan mode, and the Omega angle is 1 °.Measuring voltage and electric current are 40kv and 30mA, take measurement of an angle 2 θ in 20～80 ° of scopes, and Step Size is 0.02 °, and Time per Step is 0.4 °/s.
XRD measurement result as shown in figure 10, oxide-film is by Fe
2O
3With Fe
3O
4Form.Mention in the related description of this result and conventional art low-temperature oxidation generated is consistent mutually.
The Fe phase has also been measured in experiment, and this is because the too thin and related signal that does not have the phase of oxidation in the band steel crust that detects of oxide-film.
In order to understand the sintering circuit condition effect, the use light microscope is observed generate oxide-film in the mode of regulating sintering temperature and sintering time under atmospheric atmosphere after, and the sintering condition of Figure 11 a is that carry out sintering processes under 300 ℃ 1 hour 30 minutes, the sintering condition of Figure 11 b are to carry out sintering processes under 500 ℃ 3 hours, the sintering condition of Figure 11 c are to carry out 1 hour oxide-film of sintering processes under 650 ℃.
It is green that the surface of Figure 11 (a) is, expression Fe
3O
4The ratio of phase is higher, and the surface of Figure 11 (b) takes on a red color, expression Fe
2O
3The ratio of phase is higher, and Figure 11 (c) is though successfully be in surface roughness factor dr/di control in 1.015～1.615 the scope, and oxide-film is fine and closely woven and swell.
For aforementioned phenomenon, we can followingly illustrate.
Because welding wire surface is a solid and the oxygen supply source is a gas, form at first that the Fe ratio far surpasses oxygen in the layer of oxide-film, therefore Fe can appear
3O
4The higher phase of content.Oxygen reacted the back growth by the oxide-film diffusion of formation at first and with Fe when the oxide-film after this was grown up.This moment, oxygen and Fe reaction back generated Fe
2O
3Or Fe
3O
4Phase, Fe
2O
3With Fe
3O
4Appearance volumetric expansion shown in the following tabulation 2 in capital.
[table 2]
| Classification | Fe | Fe 3O 4 | Fe 2O 3 |
| Solid density (g/cm 3) | 7.87 | 5.16 | 5.20 |
| 1 molal weight (g) | 55.85 | 231.55 | 159.70 |
| The reaction back is at the weight change (g) of 1 mole of Fe | 55.85 | 77.18 | 79.85 |
| The reaction back is at the Volume Changes (cm of 1 mole of Fe 3) | 7.097 | 14.957 | 15.356 |
| Cubical expansivity (%) | 100 | 211 | 216 |
Aforesaid volumetric expansion will cause stress between oxide-film and band steel crust, aforesaid stresses can reduce the adhesive capacity of oxide-film, and then influences resistance to rust and wire feeding property.Oxide-film is thick more, and stress is big more.
Learn that thus Figure 11 (b) grows up owing to oxide-film is excessive with Figure 11 (c) and improved Fe
2O
3Ratio, reduced the adhesive capacity of oxide-film, and then reduced resistance to rust and wire feeding property.
Embodiment 3
Present embodiment has shown for the resistance to rust that improves the sintering flux-cored wire that is used for gas shielded arc welding and wire feeding property and the oxide thickness of needs.
Oxide-film measuring method of the present invention is as follows.
1. to become 90 ° direction to cut off welding wire with respect to length direction.
2. use the welding wire after the resin support is cut off and it is erect along vertical direction.
3. polish processing to being supported test piece successively from No. 200～No. 1500 husky cloth.
4. spreading diamond glass (diamond paste) and polish on abrasive cloth according to the order of 6 μ m, 3 μ m and 1 μ m.
5. utilize ultrasonic wave that the welding wire that polishing finishes was cleaned about 10 minutes.
6. fully dry at the oven below 100 ℃ and cleaned the test piece that finishes.
7. use the see drying oxide thickness of welding wire of the backscattering electronics of SEM.
8. get its mean value after measuring the thickness of 4 arbitrary finished surfaces.
In order to measure oxide thickness, under atmospheric atmosphere, changed temperature and time successively.Experiment can using gases stove and electric furnace, and present embodiment has used electric furnace.
Tabulate down and 3 shown the finished surface oxide thickness under all temps and time and the uniformity of finished surface oxide-film.
[table 3]
| No. | Sintering temperature (℃) | Sintering time (time: minute) | Oxide thickness (μ m) | The uniformity of oxide-film |
| 1 | 200 | 10:00 | 0.08 | × |
| 2 | 300 | 12:00 | 0.90 | ○ |
| 3 | 300 | 5:00 | 0.49 | ○ |
| 4 | 300 | 1:30 | 0.10 | ○ |
| 5 | 400 | 8:00 | 0.89 | ○ |
| 6 | 400 | 3:00 | 0.34 | ○ |
| 7 | 400 | 0:50 | 0.10 | ○ |
| 8 | 500 | 3:00 | 0.93 | ○ |
| 9 | 500 | 1:00 | 0.30 | ○ |
| 10 | 500 | 0:30 | 0.11 | ○ |
| 11 | 570 | 1:30 | 1.08 | ○ |
| 12 | 570 | 0:20 | 0.10 | ○ |
| 13 | 650 | 1:00 | 1.46 | × |
| 14 | 650 | 0:30 | 0.76 | × |
| 15 | 650 | 0:10 | 0.09 | × |
(upward the determination methods to the oxide-film uniformity is as follows in the table: after measuring the finished surface oxide thickness of any 4 faces, standard deviation is lower than at 20% o'clock and is judged as zero, surpass 20% to be judged as *.)
As shown in table 3, sintering temperature is more than 300 ℃～570 ℃ Nos.2, and 3,4,5,6,7,8,9,10,11,12 lubricant can fully decompose, and increases the sintering processes time oxide thickness is and then increased, and the uniformity of oxide-film also can be optimized.
But the finished surface oxide thickness of No.1 that carries out sintering processes under 200 ℃ of temperature is extremely thin, and the uniformity is also bad.This is because when carrying out sintering processes under 200 ℃ of temperature, sintering temperature does not reach the organic substance decomposition temperature of lubricant, organic substance is not decomposed, and the lubricant that do not have to decompose has covered contacting between welding wire surface and the oxygen, has stoped the generation and the growth of oxide-film.The position that does not have lubricant in the welding wire surface is owing to contact oxygen has formed oxide-film and growth.So, caused the phenomenon of position with oxide-film and the position coexistence that does not have oxide-film, not only reduced resistance to rust, the uneven phenomenon of oxide-film also occurred on surperficial uniform processing surface.
The sintering temperature of Nos.13～15 has reached 650 ℃, and the generation of its oxide-film and growth rate are very fast.When comparing with the position that does not have lubricant at the position that has lubricant on the welding wire surface, the lubricant of welding wire surface can absorb latent heat and decompose, generate oxide-film and growth then, do not have the welding wire surface of lubricant that oxide-film is generated and growth fast.Whether residual generation and the growth to oxide-film of the lubricant of welding wire surface caused temporal difference, even aforementioned time difference is very little, also accelerated oxidation reaction speed, even therefore on surperficial uniform processing surface, can not obtain the good oxide-film of the uniformity owing to temperature is high.Aforementioned deviation is more obvious when the oxide thickness of finished surface relatively, concavo-convex and sunk surface, even surface roughness factor value dr/di has met limited range 1.015～1.615 of the present invention, its wire feeding property and resistance to rust are also bad.
In addition, the sintering temperature of No.15 and time control are bad, make that the uniformity of oxide-film and thickness are all undesirable.Generally speaking, for the oxide thickness that makes finished surface meets the condition of 0.10～0.90 μ m and forms uniform oxide-film, should under 300 ℃～570 ℃ temperature, carry out 20 minutes～12 hours sintering processes.
As previously mentioned, suitably regulate welding wire surface roughness and oxide thickness, can improve the wire feeding property and the resistance to rust of sintering flux-cored wire.
Embodiment 4
The influence that the actual arc length of welding wire surface circular arc (dr) that present embodiment has shown the sintering flux-cored wire is risen for the wire feeding property and the resistance to rust of flux-cored wire the oxide thickness at the ratio (dr/di) of circular arc performance length (di) and finished surface position.
The welding wire of the embodiment of the invention has used the sintering welding wire, and its specification is the E71T-1 of AWS specification, YFW-C50DR grade products 1.4 Ф of JIS specification.Welding wire surface rugosity factor this moment (dr/di) uses the method among the previous embodiment 1-3 to measure with the oxide thickness of finished surface, surveys its wire feeding property and resistance to rust then.In measuring the salt spraytest of resistance to rust, under experimental condition, whether to get rusty through observing after 20 minutes, its resistance to rust of tense marker of getting rusty is *, its resistance to rust of tense marker of not getting rusty is zero.Welding wire uses the size of 1.4 Ф, salt spray condition such as table 4.
[table 4]
| Salt spray condition | |
| Indoor temperature: 35 ℃ | The temperature inside the box: 50 ℃ |
| Brine strength: NaCl 5% | Brine spray pressure: 0.15Mpa |
After the long new wire feed conduit of 5m twined 2 times (loop coil) around the diameter of 300mm, 5 welding condition had been carried out the wire feeding property assessment according to tabulating down.
[table 5]
| Welding condition during the assessment wire feeding property | The welding posture | |
| Electric current (A): 270 | Voltage (V): 34 | Bead on Plate |
| Speed (cm/min): 35 | Weld interval (sec) :- | |
| Gas: CO 2 100％ | Gas flow (l/min): 20 | |
The assessment benchmark of wire feeding property is as follows: not enough 80sec of welding duration, in the time of can't welding because feeding has some setbacks, judge that wire feeding property is bad and be labeled as *, can continue to weld 100sec when above, its wire feeding property is labeled as zero, and the time is judged as general wire feeding property and is labeled as △ between 80～100sec the time.
Table 6 has been put the assessment result of present embodiment in order.
[table 6]
| Classification | Welding wire surface rugosity factor (dr/di) | The oxide thickness of finished surface (μ m) | Wire feeding property | Resistance to rust |
| Comparative Examples 1 | 1.689 | 0.17 | × | ○ |
| Comparative Examples 2 | 1.376 | 0.08 | ○ | × |
| Comparative Examples 3 | 1.706 | 1.13 | × | × |
| Comparative Examples 4 | 1.721 | 0.09 | × | × |
| Comparative Examples 5 | 1.012 | 0.34 | △ | ○ |
| Comparative Examples 6 | 1.014 | 1.08 | × | × |
| Comparative Examples 7 | 1.010 | 0.06 | × | × |
| Comparative Examples 8 | 1.048 | 0.93 | △ | × |
| Comparative Examples 9 | 1.732 | 0.53 | × | × |
| Comparative Examples 10 | 1.204 | 1.46 | × | × |
| Embodiment 1 | 1.615 | 0.10 | ○ | ○ |
| Embodiment 2 | 1.582 | 0.76 | ○ | ○ |
| Embodiment 3 | 1.015 | 0.90 | ○ | ○ |
| Embodiment 4 | 1.454 | 0.90 | ○ | ○ |
| Embodiment 5 | 1.612 | 0.30 | ○ | ○ |
| Embodiment 6 | 1.364 | 0.16 | ○ | ○ |
| Embodiment 7 | 1.274 | 0.10 | ○ | ○ |
| Embodiment 8 | 1.265 | 0.49 | ○ | ○ |
| Embodiment 9 | 1.615 | 0.90 | ○ | ○ |
| Embodiment 10 | 1.143 | 0.89 | ○ | ○ |
| Embodiment 11 | 1.087 | 0.11 | ○ | ○ |
| Embodiment 12 | 1.015 | 0.10 | ○ | ○ |
| Embodiment 13 | 1.018 | 0.16 | ○ | ○ |
As shown in table 6, Comparative Examples 1 has exceeded limited range of the present invention with welding wire surface rugosity factor (dr/di) value of Comparative Examples 9, ignition tip when therefore having increased welding wire feeding and the friction resistance between the wire feed conduit, and then reduced wire feeding property.
Wherein, the welding wire surface rugosity factor (dr/di) of Comparative Examples 1 is though value has exceeded limited range of the present invention, and resistance to rust is still good, and this is because the oxide thickness of finished surface is controlled in 0.17 μ m, below aforementioned phenomenon is further specified.
The oxide thickness of finished surface is thinner, and the condition that expression allows oxide-film to grow up is shorter, represents that also the difference between the oxide thickness at finished surface and concavo-convex and the position of caving in is less.Therefore, though the welding wire surface roughness has caused the thickness deviation of each position of welding wire (finished surface, concavo-convex and sunk surface) oxide-film, do not have influence on resistance to rust because deviation is little.
On the contrary, the welding wire surface of Comparative Examples 9 is coarse, and oxide thickness is 0.53 μ m, because oxide-film has been grown up to a certain degree, causes the oxide thickness and the property difference at each position of welding wire, has therefore occurred rust staining when resistance to rust is tested.
The finished surface oxide thickness of Comparative Examples 2 is too thin, and the oxide-film that can't distribute equably on the welding wire surface does not then form oxide-film on a part of surface, has therefore occurred rust staining when resistance to rust is tested.
Welding wire surface rugosity factor (dr/di) value and the finished surface oxide thickness of Comparative Examples 3 have all exceeded higher limit of the present invention, therefore each position property difference of welding wire surface oxide-film is bigger, the fine and closely woven property of oxide-film is relatively poor, causes wire feeding property and resistance to rust bad.
Welding wire surface rugosity factor (dr/di) value of Comparative Examples 4 is too high, and the friction during feeding between ignition tip and the wire feed conduit increases, and then has influenced wire feeding property; Because the oxide thickness of finished surface is thinner relatively, does not then form oxide-film on a part of surface, therefore rust staining has appearred when resistance to rust is tested.
The welding wire surface rugosity factor (dr/di) of Comparative Examples 5～7 value is too low, has reduced the maintenance energy that sticks to the feeding lubricant on the welding wire surface in order to improve the wire feeding property after the sintering processes, and then has reduced welding wire feeding.The finished surface oxide thickness of Comparative Examples 6 is too thick, the fine and closely woven property deficiency of oxide-film, Fe
2O
3Ratio increase, cause resistance to rust bad.Comparative Examples 7 does not then form oxide-film because the oxide thickness of finished surface is too thin on a part of surface, therefore occurred rust staining when resistance to rust is tested.
The welding wire surface rugosity factor (dr/di) of Comparative Examples 8 and Comparative Examples 10 is though be worth in limited range of the present invention, but the oxide thickness of finished surface is too thick, cause the fine and closely woven property of oxide-film bad, and then make wire feed conduit and ignition tip interior oxidation film peel off and accumulate, cause welding wire feeding bad, Fe
2O
3Ratio improve, cause resistance to rust bad.
Welding wire surface rugosity factor (dr/di) value of embodiment 1 to embodiment 13 maintains in 1.015～1.615 the scope, and the oxide thickness of finished surface maintains in the scope of 0.10～0.90 μ m, the Fe of resistance to rust excellence when therefore generating oxide-film
3O
4Ratio is higher, and the oxide-film property difference at each position of welding wire is less, can generate fine and closely woven oxide-film, and then has improved resistance to rust and wire feeding property.
The invention effect
As previously mentioned, when carrying out sintering processes the surface roughness of welding wire and oxide thickness are controlled in the particular range, have improved the Fe of resistance to rust excellence3O
4Phase ratio, the deviation of each position of welding wire (finished surface, concavo-convex and sunk surface) is less, and the oxide-film of generation is thinner and fine and closely woven, can be at the fine oxide-film of ignition tip inner accumulation when therefore welding.
Sintering flux-cored wire for gas shielded arc welding provided by the invention, its resistance to rust and wire feeding property are better than traditional sintering flux-cored wire that is used for gas shielded arc welding.
Claims (3)
1. sintering flux-cored wire that is used for gas shielded arc welding; wherein through the flux-cored wire surface of sintering processes by smooth finished surface, convex-concave surface, and with respect to finished surface be negative direction promptly towards the direction at welding wire center and surfacewise the depression that forms of circumferencial direction formed blending surface, it is characterized by:
The oxide thickness of described smooth finished surface is in 0.10～0.90 mu m range; The actual arc length dr of circular arc is in the ratio dr/di of circular arc performance length d i in 1.015～1.615 the scope.
2. the sintering flux-cored wire that is used for gas shielded arc welding according to claim 1 is characterized by:
Described oxide-film is by Fe
2O
3And Fe
3O
4Form.
3. a manufacture method that is used for the sintering flux-cored wire of gas shielded arc welding comprises band steel crust is carried out the operation that tubulation, filling solder flux, drawing, sintering and surface conditioning agent apply, and it is characterized by:
The surface roughness of described band steel crust is as the criterion with the Ra value and is controlled in the scope of 0.20～1.43 μ m, the drawing speed of described tubulation operation is controlled in the scope of 20～150m/min, the second stage drawing speed then is controlled in the scope of 100～1800m/min, carries out described sintering circuit 20 minutes to 12 hours in 300～570 ℃ of temperature ranges under the general atmosphere atmosphere.
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| KR1020050133022 | 2005-12-29 | ||
| KR1020050133022A KR100668170B1 (en) | 2005-12-29 | 2005-12-29 | Baked flux cored wire for gas shield arc welding having excellent rust resistance and feedability and a method for preparing thereof |
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| Publication Number | Publication Date |
|---|---|
| CN1990160A true CN1990160A (en) | 2007-07-04 |
| CN100503132C CN100503132C (en) | 2009-06-24 |
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|---|---|---|---|
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| KR (1) | KR100668170B1 (en) |
| CN (1) | CN100503132C (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102172804A (en) * | 2011-02-22 | 2011-09-07 | 罗崇墉 | CO2 gas shielded arc welding solid wire produced by using oxidation process and manufacturing method thereof |
| CN102909495A (en) * | 2012-10-08 | 2013-02-06 | 韩永艾 | Method for producing CO2 gas shield solid welding wire by physical oxidation method |
| CN109821925A (en) * | 2019-01-29 | 2019-05-31 | 张正周 | A kind of production technology of composite pipe |
Family Cites Families (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS58205697A (en) | 1982-05-24 | 1983-11-30 | Kobe Steel Ltd | Production of flux cored wire for welding |
| JPS59232697A (en) | 1983-06-15 | 1984-12-27 | Kobe Steel Ltd | Production of flux cored wire |
| JPS62110897A (en) | 1985-11-11 | 1987-05-21 | Kobe Steel Ltd | Iron power flux cored wire |
| JPH11197878A (en) | 1998-01-08 | 1999-07-27 | Nippon Steel Weld Prod & Eng Co Ltd | Wire for gas shielded arc welding and its manufacture |
| JP2000237894A (en) | 1999-02-16 | 2000-09-05 | Nippon Steel Weld Prod & Eng Co Ltd | Flux cored wire for gas shielded arc welding and its production |
-
2005
- 2005-12-29 KR KR1020050133022A patent/KR100668170B1/en active IP Right Grant
-
2006
- 2006-11-28 CN CNB200610144881XA patent/CN100503132C/en active Active
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102172804A (en) * | 2011-02-22 | 2011-09-07 | 罗崇墉 | CO2 gas shielded arc welding solid wire produced by using oxidation process and manufacturing method thereof |
| CN102909495A (en) * | 2012-10-08 | 2013-02-06 | 韩永艾 | Method for producing CO2 gas shield solid welding wire by physical oxidation method |
| CN109821925A (en) * | 2019-01-29 | 2019-05-31 | 张正周 | A kind of production technology of composite pipe |
Also Published As
| Publication number | Publication date |
|---|---|
| CN100503132C (en) | 2009-06-24 |
| KR100668170B1 (en) | 2007-01-11 |
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