CN106232287A - The bonding layer submerged-arc welding method of high Cr system CSEF steel - Google Patents
The bonding layer submerged-arc welding method of high Cr system CSEF steel Download PDFInfo
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- CN106232287A CN106232287A CN201580022331.8A CN201580022331A CN106232287A CN 106232287 A CN106232287 A CN 106232287A CN 201580022331 A CN201580022331 A CN 201580022331A CN 106232287 A CN106232287 A CN 106232287A
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- mass
- bonding layer
- welding
- submerged
- arc welding
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Classifications
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K9/00—Arc welding or cutting
- B23K9/18—Submerged-arc welding
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
- B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
- B23K35/24—Selection of soldering or welding materials proper
- B23K35/30—Selection of soldering or welding materials proper with the principal constituent melting at less than 1550 degrees C
-
- 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
- B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
- B23K35/36—Selection of non-metallic compositions, e.g. coatings, fluxes; Selection of soldering or welding materials, conjoint with selection of non-metallic compositions, both selections being of interest
- B23K35/362—Selection of compositions of fluxes
-
- 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
- B23K9/23—Arc welding or cutting taking account of the properties of the materials to be welded
Abstract
There is provided a kind of in the submerged-arc welding of high Cr system CSEF steel, just can suppress the welding method that bonding layer heat cracking occurs without increasing step labor intensity.It is characterized in that, will be containing below C:0.10 mass %, below Si:0.50 mass %, below Mn:1.50 mass %, below P:0.025 mass %, below S:0.025 mass %, metal dust that surplus is made up of Fe and inevitable impurity or wire shot 21f, fill in the groove of mother metal 10 to spreading height h:1.0～4.0mm, carry out bonding layer welding.In bonding layer welds, the fusing point of the 21f suppression welding metals such as described metal dust decline, it is possible to prevent heat cracking.
Description
Technical field
The present invention relates to high Cr system CSEF (Creep Strength-Enhanced Ferritic steel: creep strength
The iron-based steel strengthened) the submerged-arc welding method of steel, particularly relate to bonding layer soldering method.
Background technology
The chemical reaction container (reactor) of thermal power generation boiler and steam turbine, desulfurization and modification (heavy oil decomposition) because
All operate under high temperature, high pressure, so as material, being suitable for 1.25Cr-0.5Mo steel, 2.25Cr-1.0Mo steel, 2.25Cr-
1.0Mo-V steel etc..In recent years, effectively utilizing and in petroleum refining at heavy oil, it is desirable to further high energy efficiency, containing 8 matter
The application of the high Cr system CSEF steel of the Cr of amount more than % is studied.In high Cr system CSEF steel, there is ASTM (American
Society for Testing and Materials: American Society for Testing Materials) specification and ASME (American
Society of Mechanical Engineers: machinery association of the U.S.) specification defined SA387Gr.91,
SA213Gr.T91 etc..
Thermal power generation boiler, steam turbine, reactor are by forging-ring, forging pipe and bending machining steel plate proper combination, welded
And assemble.Here, such as forging-ring also can become thickness of slab 150～450mm, maximum outside diameter 7m is weak, total long number～number 10m.As
Welding method, can use shielded arc welding, TIG (Tungsten Inert Gas: gas tungsten arc welding) weldering, submerged arc
Weldering, especially because submerged-arc welding more high energy efficiency compared with other welding method, so being used more., if to high Cr
It is that CSEF steel carries out submerged-arc welding, then bonding layer welding is susceptible to heat cracking.
The heat cracking welded as the bonding layer of submerged-arc welding prevents technology, such as, disclosed in patent documentation 1, making
For high-carbon steel C content 0.27 mass % JIS SF50 and ASTM A148 narrow groove submerged-arc welding in, as spacer, make C
In the different material of foreign body that mild steel below content 0.10 mass % and welding metal are constituted joint between mother metal, specifically
For be the technology of bonding layer position between V groove or X groove.This patent documentation 1 describes, at the narrow groove of high-carbon steel
In welding, why it is susceptible to heat cracking at its bonding layer weld seam, is that the C because describing the mother metal that mother metal dilution causes is to welding
The increase of metal.That is, owing to the C concentration of welding metal uprises, fusing point reduces, and causes heat cracking to be susceptible to.Therefore, exist
Disclosed in patent documentation 1, in bonding layer welds, by the steel of low-carbon (LC) and the welding different material of foreign body that constituted of metal
Weld on spacer, the impact of the carburetting from mother metal can be relaxed, prevent heat cracking.
Prior art literature
Patent documentation
Patent documentation 1: Japanese Laid-Open Patent Publication 58-68481 publication
The problem that invention is to be solved
Here, in high Cr system CSEF steel, about C content, such as ASTM A182F91 is 0.08～0.12 mass %,
Greatly 0.12 mass %, is same journey with existing 1.25Cr-0.5Mo steel, 2.25Cr-1.0Mo steel, 2.25Cr-1.0Mo-V steel
Degree.But, with high Cr system CSEF steel by as the welding wire that constituted of material than 1.25Cr-0.5Mo steel, 2.25Cr-1.0Mo steel,
The resistance of 2.25Cr-1.0Mo-V steel is high, and therefore joule heat is high, if the size of welding current is identical, is then easier to melted.
Therefore, in the welding of high Cr system CSEF steel, the amount (deposition amount) of deposited metal becomes many, the solidification shrinkage amount of deposited metal in addition
Than 1.25Cr-0.5Mo steel, 2.25Cr-1.0Mo steel, 2.25Cr-1.0Mo-V steel more greatly, so the suppression of heat cracking is more felt sleepy
Difficult.
It addition, in order to weld slab with high energy efficiency, effectively improve weld heat input, i.e. strengthen welding current, improve
Arc voltage, reduces speed of welding.But, if improving weld heat input, during the narrowest groove, weld bead shape easily becomes
Pyriform, the occurrence risk of heat cracking uprises.So as the heat cracking of problem, be P contained in deposited metal, S,
The low-melting compound of Si, Nb etc., when solidification, at interdendritic and austenite recrystallization cyrystal boundary segregation, adds welding contraction strain
And the crackle occurred.One of Retraining Measures accordingly, as heat cracking, effectively by the composition of bonding wire, specifically, be
Through ultra-high purity (EHP:Extra High Purity) melting, the impurity such as P, S are suppressed at below 100ppm.But, due to super
High-purity melting has to use electronic torch melting and special special furnace wall fire proofed wood, so economically there is difficult point.Therefore,
Require the technology also being able to suppress heat cracking to occur under general impurity level.
Additionally, in order to apply the spacer described in patent documentation 1, it may occur that built-up welding interlayer or the setting of spacer, fixing,
The great operation labor intensity of accuracy control etc..It addition, because the different material of foreign body composition and mother metal differed widely is made
For spacer, so also including weld part, it is possible to it is unsatisfactory for the level of security of required joint performance.At patent literary composition
Offer and remove Liner Ferrule by planing after describing welding in 1, but the spacer being silent on being soldered to remove this weldering certainly
Connect metal.I.e. patent documentation 1 it is considered that, to allow spacer as the different material of foreign body in the purposes of the residual within joint
For object.Therefore, using the different material of foreign body as the welding method of the patent documentation 1 of spacer, connect from productivity ratio economy
The such viewpoint of level of security of head performance is set out, and is difficult to be applicable to thermal power generation boiler etc..
Summary of the invention
The present invention is formed in view of described problem points, and its problem is, it is provided that a kind of submerged-arc welding at high Cr system CSEF steel
In, without increasing step labor intensity, it becomes possible to the bonding layer submerged-arc welding method that suppression bonding layer heat cracking occurs.
For solving the means of problem
The present inventor etc. are through concentrating on studies, and its result is expected, by filling the filler of the composition of regulation at groove, from
And suppress the fusing point of the welding metal of bonding layer to decline.
That is, the bonding layer submerged-arc welding method of the present invention is characterised by, with high Cr system CSEF steel as mother metal, and will be containing C:0.10
Below quality %, below Si:0.50 mass %, below Mn:1.50 mass %, below P:0.025 mass %, S:0.025 matter
Amount below %, metal dust that surplus is made up of Fe and inevitable impurity or wire shot, the distribution with 1.0～4.0mm is high
Weld in degree is filled into the groove of described mother metal.
According to this method, control the filler below setting by C content and mother metal can be suppressed to dilute, welding metal
Fusing point will not reduce, and can prevent bonding layer heat cracking.
In the bonding layer submerged-arc welding method of the present invention, preferably welding wire contain C:0.03～0.13 mass %, Si:0.05～
Below 0.50 mass %, Mn:0.50～2.20 mass %, P:0.015 mass %, below S:0.010 mass %, Ni: be higher than
0.20 mass % below 1.00 mass %, Cr:8.00～10.50 mass %, Mo:0.20～1.20 mass %, V:0.05
～0.45 mass %, Nb:0.020～0.080 mass %, N:0.02～0.08 mass %, surplus is Fe and the most miscellaneous
Matter.
According to this method, it is possible to more reliably prevent bonding layer heat cracking.
In the bonding layer submerged-arc welding method of the present invention, preferably welding wire is possibly together with below Cu:1.70 mass %, B:0.005
More than at least 1 selected in the group constituted below quality %, below W:2.0 mass % and below Co:3.0 mass %.
According to this method, it is possible to the toughness that the δ-ferritic residual in suppression welding metal causes deteriorates or improves compacted
Become fracture strength.
In the bonding layer submerged-arc welding method of the present invention, be preferred for the basicity that is expressed from the next of solder flux of welding be 1.0～
3.3。
Basicity=(CaF2+CaO+MgO+SrO+Na2O+Li2O+1/2(MnO+FeO))/(SiO2+1/2(Al2O3+TiO2+
ZrO2))
Here, each compound represents the content (quality %) of each compound in solder flux gross mass.
According to this method, it is possible to the oxygen amount of suppression welding metal, and the outward appearance of welding bead and shape can be suppressed not
Good generation.
In the bonding layer submerged-arc welding method of the present invention, preferably bonding layer submerged-arc welding method is bonding layer monofilament submerged-arc welding method, its
Weld with following condition: making welding wire give speed (V) is 50～120g/min, and speed of welding (v) is 20～60cm/min,
By described welding wire give the deposition amount (V/v) of the per unit weld length that the ratio of speed and described speed of welding is tried to achieve be 1.8～
4.5g/cm。
According to this method, it is possible to more reliably suppression incomplete fusion and slag inclusion, it additionally is able to more reliably suppress high anneal crack
The generation of stricture of vagina.
In the bonding layer submerged-arc welding method of the present invention, preferably bonding layer submerged-arc welding method is bonding layer series connection submerged-arc welding method, its
Weld with following condition: make the welding wire of backward electrode give speed VLBeing 45～90g/min, the welding wire of rear row pole gives speed
VTBeing 60～110g/min, speed of welding v is 30～55cm/min, and the deposition amount of per unit length is 2.8～3.8g/cm.
According to this method, it is possible to the reduction of suppression welding efficiency, it additionally is able to more reliably suppress sending out of heat cracking
Raw.
In the bonding layer submerged-arc welding method of the present invention, preferred nozzle/mother metal spacing is 20～40mm.
According to this method, it is possible to suppression deposition amount is superfluous, it additionally is able to suppress spray nozzle front end by electric arc melting loss.
In the bonding layer submerged-arc welding method of the present invention, it is the scope of 0 ° to 60 ° about nozzle angle, preferably back rake angle α, front
Angle of inclination beta is the scope of 0 ° to 60 °.
According to this method, it is possible to easily make welding wire feed speed stabilisation.
In the bonding layer submerged-arc welding method of the present invention, preferred nozzle is shaped as straight tube-like or elbow shape.
According to this method, it is possible to easily make welding wire feed speed stabilisation.
In the bonding layer submerged-arc welding method of the present invention, bonding layer submerged-arc welding method is bonding layer series connection submerged-arc welding method, backward electrode
And the anode-cathode distance between rear row pole is 15mm～25mm.
According to this method, it is possible to obtain good weld bead shape.
Invention effect
Bonding layer submerged-arc welding method according to the present invention, in the welding of high Cr system CSEF steel, works without increasing step
Intensity, it becomes possible to the generation of suppression bonding layer heat cracking.
Accompanying drawing explanation
Fig. 1 is the front view of the state of the tip of the monofilament mode of the submerged-arc welding method representing the present invention.
Fig. 2 is the front view of the state of the tip of the monofilament mode of the submerged-arc welding method representing the present invention.
Fig. 3 is the front view of the state of the tip of the monofilament mode of the submerged-arc welding method representing the present invention.
Fig. 4 is the front view of the state of the tip of the series system of the submerged-arc welding method representing the present invention.
Fig. 5 is the shape of the narrow groove of the mother metal of the bonding layer submerged-arc welding method representing the present invention and cuing open of bonding layer welding metal
Face figure.
Fig. 6 is shape and the welding gold of series system formation of the narrow groove of the mother metal of the submerged-arc welding method representing the present invention
The profile of the stacking main points belonged to.
Fig. 7 is the profile of the spread state of the filler before the welding of the bonding layer submerged-arc welding method representing the present invention, phase
When in the partial enlarged drawing of Fig. 5.
Fig. 8 is the front view of the tip of the submerged-arc welding method for the present invention.
Fig. 9 is the side view of the tip shown in Fig. 8.
Figure 10 is the end view drawing that the welding wire of the tip interpolation shown in Fig. 8 highlights side, is the bottom view relative to Fig. 9.
Figure 11 is the front view of the state of the tip of the monofilament mode of the submerged-arc welding method representing the present invention.
Figure 12 is the front view of the state of the tip of the monofilament mode of the submerged-arc welding method representing the present invention.
Figure 13 is the front view of the state of the tip of the monofilament mode of the submerged-arc welding method representing the present invention.
Figure 14 is the front view of the state of the tip of the monofilament mode of the submerged-arc welding method representing the present invention.
Figure 15 is the front view of the state of the tip of the monofilament mode of the submerged-arc welding method representing the present invention.
Figure 16 is the front view of the state of the tip of the monofilament mode of the submerged-arc welding method representing the present invention.
Detailed description of the invention
Hereinafter, the mode for the enforcement of the present invention is illustrated in detail.
The bonding layer submerged-arc welding method (following, the bonding layer soldering method of the present invention) of the present invention is the submerged-arc welding of high Cr system CSEF steel
Bonding layer weldering method, monofilament, series connection any one mode the most applicable.In monofilament submerged-arc welding, such as, shown in Fig. 1～3, make
With the interior tip 11 being inserted with welding wire 12, with arc welding, mother metal 10 is welded, make the angle (nozzle angle) of 1 tip 11
Lean forward (Fig. 1) relative to welding direction or hypsokinesis (Fig. 2) or vertical (Fig. 3).On the other hand, in series connection submerged-arc welding, such as Fig. 4 institute
Show, be use simultaneously 2 respectively in be inserted with backward electrode (tip) 11a and rear row pole (tip) 11b of welding wire 12a, 12b and weld
Connect.In addition, in submerged-arc welding, monofilament, each mode of series connection all use not shown solder flux.It addition, about nozzle/mother metal spacing,
Nozzle form, nozzle angle, aftermentioned be illustrated.
The bonding layer soldering method of the present invention applies to the first layer, i.e. the submerged-arc welding method of bonding layer weldering.Welded by bonding layer, as
Shown in Fig. 5, the bottom land solidification in groove of the bonding layer welding metal 21.Thereafter, by making layer repeatedly, as Fig. 6 shows, new welding
Metal 22 (the white hollow out direction of arrow along figure) is laminated to above.
(mother metal)
In the bonding layer soldering method of the present invention, as mother metal (welded material), with high Cr system CSEF steel as object.High Cr system
CSEF steel has all size, such as, and SA387Gr.T91, the EN specification (European of ASTM specification and ASME specification defined
Standards: European requirements) X10CrMoVNb9-1 of defined, the fiery SFVAF28 of firepower technical standard defined, fire
SFVAF29, fire STBA28, fire STPA28 fire, SCMV28.
As the composition of mother metal, preferably comprise below C:0.07～0.14 mass %, Si:0.50 mass %, Mn:0.70 matter
Below amount below %, Ni:0.50 mass %, Cr:8.00～11.50 mass %, Mo:0.25～1.10 mass %, V:0.15～
Below 0.35 mass %, Nb:0.04～0.10 mass %, P:0.025 mass %, below S:0.015 mass %, N:0.03～
0.10 mass %, surplus is made up of Fe and inevitable impurity, in addition it is also possible to possibly together with below Cu:1.70 mass %, B:
Less than 0.060%, below below W:2.50%, Co:3.0 mass %.
In the bonding layer soldering method of the present invention, preferably make the mother metal of described composition and welding wire described later and solder flux in addition group
Close.In the bonding layer soldering method of this external present invention, as it is shown in fig. 7, by the filler 21f of following predetermined component dissipating with regulation
Weld in cloth height h is filled into groove.
(filler)
In the bonding layer soldering method of the present invention, will containing below C:0.10 mass %, below Si:0.50 mass %, Mn:
Below 1.50 mass %, below P:0.025 mass %, below S:0.025 mass %, surplus is by Fe and inevitable impurity structure
The metal dust become or wire shot are as filler, with 1.0～4.0mm spread and highly-filled carry out in the groove of mother metal
Welding.Hereinafter, filler is illustrated in more detail.
(below C:0.10 mass %)
C, in deposited metal, makes fusing point reduce and cause heat cracking.In order to prevent the fusing point of deposited metal from declining, fill out
The C content filling agent is additionally contemplates that mother metal dilutes, and is below 0.10 mass %, below preferably 0.05 mass %.
(below Si:0.50 mass %)
The viscosity of Si regulation motlten metal, has the effect arranging weld bead shape.On the other hand, if higher than 0.50 matter
Amount %, then slag burns sticky hair life, and slag removes difficulty.Therefore, the Si content of filler is below 0.50 mass %, is preferably
Below 0.30 mass %.
(below Mn:1.50 mass %)
The viscosity of Mn regulation motlten metal, has the effect arranging weld bead shape.On the other hand, if higher than 1.50 matter
Amount %, then slag burns sticky hair life, and slag removes difficulty.Therefore, the Mn content of filler is below 1.50 mass %, is preferably
Below 1.30 mass %.
(below P:0.025 mass %, below S:0.025 mass %)
P, S, in deposited metal, make fusing point reduce respectively, cause heat cracking.Therefore, each content of P, S of filler
It is below 0.025 mass %, preferably less than 0.025 mass %.
In filler, as inevitable impurity, it is also possible to containing Cu, Cr, Mo, Ni, Nb, V, W, Co, N etc. each 0.5
Below quality %, add up to below 0.8 mass %.
(spreading highly: 1.0～4.0mm)
When the distribution of filler is highly less than 1.0mm, the amount of filler is not enough, it is impossible to the C of the deposited metal of suppression bonding layer
Thickening, result is, the C concentration excess of deposited metal, it is impossible to suppression heat cracking.Therefore, in filler so that it is spread height
For more than 1.0mm, preferably more than 1.5mm.On the other hand, if filling filler higher than spreading height 4.0mm, then filler
Quantitative change obtain superfluous, weld shape becomes projection welding road, causes incomplete fusion and slag inclusion.Therefore, for filler, spread height
For below 4.0mm, preferably below 3.5mm.
Filler be suitable for the metal dust of described composition, wire shot any one can.Metal dust is average
Particle diameter is below 1mm, and the preferred string diameter of wire shot and length (Cutting Length) are respectively preferably below 1mm.
Further, after whole welding after also including the second layer is complete, weld part (Fig. 5 that filler is formed
Shown bonding layer welding metal 21) can also remove according to the level of security of required joint performance.Removing method can
It is suitable for the known method such as planing, machining.
(welding wire)
The welding wire used in the bonding layer soldering method of the present invention, preferably comprise C:0.03～0.13 mass %, Si:0.05～
0.50 mass %, Mn:0.50～2.20 mass %, Ni: higher than 0.20 mass % and below 1.00 mass %, Cr:8.00～
10.50 mass %, Mo:0.20～1.20 mass %, V:0.05～0.45 mass %, Nb:0.020～0.080 mass %, P:
Below 0.015 mass %, below S:0.010 mass %, N:0.02～0.08 mass %, surplus is by Fe and inevitable impurity
Constitute, in addition it is also possible to containing below Cu:1.70 mass %, below B:0.005 mass %, below W:2.0 mass %, Co:
Below 3.0 mass %.
Together with C with N, be combined with Cr, Mo, W, V, Nb, B and separate out various carbonitride, have and make creep rupture strength carry
High effect.In order to obtain this effect fully, the C content of welding wire is preferably more than 0.03 mass %, and more preferably 0.04
More than quality %.On the other hand, if add C superfluously, if C content is higher than 0.13 mass %, the most high temperature resistant crackle specifically
Property deterioration.Therefore, the C content of welding wire is preferably below 0.13 mass %, below more preferably 0.12 mass %.
Si works as deoxidizer, reduces the oxygen amount in deposited metal, has the effect of the toughness improving welding metal.
In order to obtain this effect fully, the Si content of welding wire is preferably more than 0.05 mass %, more preferably higher than 0.05 matter
Amount %.On the other hand, Si is ferrite generating elements, if add superfluously, if Si content is higher than 0.50 mass % specifically,
Then cause the δ-ferritic residual in welding metal, the toughness deterioration of welding metal.Therefore, the Si content of welding wire is preferably
Below 0.50 mass %, below more preferably 0.48 mass %, more preferably below 0.45 mass %.
Mn works as deoxidizer, reduces the oxygen amount in deposited metal, has the effect improving toughness.It addition, Mn is
Austenite generates element, has the effect suppressing the toughness caused because of the δ-ferritic residual of welding metal to deteriorate.In order to fill
Dividing ground to obtain these effects, the Mn content of welding wire is preferably more than 0.50 mass %, more than more preferably 0.55 mass %.Another
Aspect, Mn content is higher than 2.20 mass %, and the toughness of welding metal also can deteriorate.Therefore, the Mn content of welding wire is preferably 2.20
Below quality %, below more preferably 2.15 mass %.
As Ni with Mn be austenite generate element, have suppress because of welding metal δ-ferritic residual cause tough
Property deterioration effect.In order to obtain this effect fully, the Ni content of welding wire is preferably above 0.20 mass %, more preferably
More than 0.25 mass %, more preferably more than 0.30 mass %.On the other hand, Ni content is higher than 1.00 mass %, welding
The toughness of metal also can deteriorate.Therefore, the Ni content of welding wire is preferably below 1.00 mass %, more preferably 0.95 mass % with
Under.
If additionally, the total content of Mn and Ni is higher than 1.50 mass %, then welding the toughness deterioration of metal, and deposition gold
The Ac1 transformation temperature belonged to reduce and cannot high tempering, it is impossible to carry out the stabilizing treatment organized.Therefore, Mn and Ni of welding wire
Total content more preferably 1.50 mass % below.
Cr be the present invention bonding layer soldering method in as the essential element of high Cr system CSEF steel of welded material (mother metal), be
For guaranteeing oxidative resistance and the integral element of elevated temperature strength.In order to obtain this effect fully, the Cr content of welding wire
It is preferably more than 8.00 mass %, more than more preferably 8.05 mass %.On the other hand, Cr is ferrite generating elements, if mistake
Add surplusly, if Cr content is higher than 10.50 mass % specifically, then cause δ-ferritic residual, the toughness of welding metal
Deterioration.Therefore, the Cr content of welding wire is preferably below 10.50 mass %, below more preferably 10.45 mass %.
Mo is solution strengthening element, has the effect making creep rupture strength improve.In order to obtain this effect fully,
The Mo content of welding wire is preferably more than 0.20 mass %, more than more preferably 0.22 mass %.On the other hand, because Mo is ferrum element
Body generates element, if so add superfluously, specifically, if making the content of Mo higher than 1.20 mass %, then causes welding gold
δ in genus-ferritic residual, the toughness deterioration of welding metal.Therefore, the Mo content of welding wire be preferably 1.20 mass % with
Under, below more preferably 1.18 mass %.
V is precipitation strength element, has the effect making creep rupture strength improve as Carbonitride Precipitation.In order to fill
Dividing ground to obtain this effect, the V content of welding wire is preferably more than 0.05 mass %, more than more preferably 0.10 mass %.Another
Aspect, V is also ferrite generating elements, if add superfluously, specifically, if V content is higher than 0.45 mass %, then causes weldering
Connect the δ in metal-ferritic residual, the toughness deterioration of welding metal.Therefore, the V content of welding wire is preferably 0.45 mass %
Hereinafter, below more preferably 0.40 mass %.
Nb carries out solution strengthening and separates out as nitride, contributes to the element of the stabilisation of creep rupture strength.For
Obtaining this effect fully, the Nb content of welding wire is preferably more than 0.020 mass %, more preferably 0.022 mass % with
On.On the other hand, Nb is also ferrite generating elements, if contain superfluously, specifically, if Nb content is higher than 0.080 matter
Amount %, then cause the δ-ferritic residual in welding metal, the toughness deterioration of welding metal.Therefore, the Nb content of welding wire is excellent
Elect below 0.080 mass % as, below more preferably 0.078 mass %.
P and S is the element improving heat cracking sensitivity respectively.P content higher than 0.015 mass % time or S content be higher than
During 0.010 mass %, high-temperature cracking resistance deteriorates.It is therefore preferable that the P content of welding wire is limited in below 0.015 mass %, more excellent
Elect below 0.010 mass % as.Additionally, it is preferred that the S content of welding wire is limited in below 0.010 mass %, more preferably 0.009 matter
Amount below %.
Together with N with C, be combined with Cr, Mo, W, V, Nb, B and separate out various carbonitride, have and make creep rupture strength carry
High effect.In order to obtain this effect fully, the N content of welding wire is preferably more than 0.02 mass %, and more preferably 0.03
More than quality %.On the other hand, if superfluously containing N, specifically, if N content is higher than 0.08 mass %, then slag fissility
Deterioration.Therefore, the N content of welding wire is preferably below 0.08 mass %, below more preferably 0.07 mass %.
Cu is that austenite generates element, has what the toughness suppressing the δ-ferritic residual in welding metal to cause deteriorated
Effect.On the other hand, if contain superfluously, specifically, if Cu content is higher than 1.70 mass %, then heat cracking is caused.Cause
This, the Cu content of welding wire is preferably below 1.70 mass %, below more preferably 1.00 mass %, more preferably 0.50 matter
Amount below %.Cu's can also be by carrying out plating to welding wire surface containing method.
B is contained by trace and makes carbide decentralized stabilization, is the effect having and improving creep rupture strength.Another
Aspect, if contain superfluously, specifically, if B content is higher than 0.005 mass %, then causes heat cracking.Therefore, the B of welding wire
Content is preferably below 0.005 mass %, below more preferably 0.003 mass %, more preferably 0.0015 mass % with
Under.
W is the solution strengthening by matrix and fine carbide precipitation, contributes to the unit of the stabilisation of creep rupture strength
Element.On the other hand, W is also ferrite generating elements, if contain superfluously, specifically, if W content is higher than 2.0 matter
Amount %, then cause the δ-ferritic residual in welding metal, the toughness deterioration of welding metal.Therefore, the W content of welding wire is preferred
It is below 2.0 mass %, below more preferably 1.8 mass %, more preferably below 1.7 mass %.
Co is the element of suppression delta ferrite residual.On the other hand, if Co surplus ground contains, specifically, if Co content is high
In 3.0 mass %, then reduce Ac1 point, therefore cannot high tempering, it is impossible to carry out the stabilizing treatment organized.Therefore, welding wire
Co content be preferably below 3.0 mass %, below more preferably 2.0 mass %, more preferably below 1.8 mass %.
In welding wire, as inevitable impurity, it is also possible to below each 0.02 mass % such as Ti, Al, add up to 0.04
Below quality %.
The preferred string diameter of welding wire is 3～5mm.This be due to string diameter less than 3mm time, it is impossible to obtain sufficient deposition amount, damage
Lose the situation of welding efficiency.On the other hand, if string diameter is higher than 5mm, then deposition amount becomes superfluous, i.e. uses the bonding layer of the present invention to weld
Method, still has the situation being difficult to suppress the heat cracking of bonding layer.
(solder flux)
The basicity being expressed from the next of the solder flux preferably used in the bonding layer soldering method of the present invention is 1.0～3.3.Basicity=
[CaF2+CaO+MgO+SrO+Na2O+Li2O+1/2(MnO+FeO)]/[SiO2+1/2(Al2O3+TiO2+ZrO2)]
Here, each compound in above formula represents this compound content (quality %) in solder flux.
When the basicity of solder flux is less than 1.0, the oxygen amount in welding metal cannot be substantially reduced, and the toughness of welding metal reduces.
Therefore, the preferred basicity of solder flux is more than 1.0, more preferably more than 1.3.On the other hand, if the basicity of solder flux is higher than 3.3, then weld
Outward appearance and the shape in road are the worst.Therefore, the preferred basicity of solder flux is less than 3.3, more preferably less than 3.2.Further, the present invention
Bonding layer soldering method in the solder flux that uses, as long as basicity meets this scope, constitute the compound of this solder flux each content etc. its
His composition, then do not have special provision.
(monofilament submerged-arc welding condition)
The bonding layer soldering method of the present invention, in the case of monofilament welds, is preferably suitable for following condition.
(nozzle/mother metal spacing)
As shown in Fig. 1～3, Figure 11～16, nozzle/mother metal spacing be the part that finally highlights from tip 11 of welding wire 12 with
Distance L between mother metal 10.As it was previously stated, as with mother metal being material, the welding wire ratio that is i.e. made up of high Cr system CSEF steel low
The resistance of Cr system CSEF steel is high, and therefore joule heat amount is big, even if under an equal amount of welding current, deposition amount also becomes many.
Here, joule heat amount is along with nozzle/mother metal spacing is elongated, change is big.Specifically, if nozzle/mother metal spacing is higher than
40mm, then deposition amount is superfluous.On the other hand, when nozzle/mother metal spacing is less than 20mm, spray nozzle front end exists by electric arc melting loss
Dangerous.Therefore, nozzle/mother metal spacing is preferably managed in the range of 20～40mm, more preferably 25～35mm
Scope.
(nozzle form)
Nozzle form is the elbow shape shown in the straight tube-like shown in Fig. 1～3, Fig. 8～10 or Japanese Patent Publication 62-58827
Such shape shown in the Fig.3b of number publication can, from guarantee giving property of welding wire and to electric position stabilisation from the viewpoint of
Suitable selection.Shown in particularly Fig. 8～10 such, make welding wire 12 prominent (with reference to Figure 11～16) spray nozzle front end portion (Fig. 8,
The lower end of Fig. 9) do not hinder welding wire give in the range of bending elbow shape nozzle, make to electric position stabilisation, result is to make weldering
Velocity-stabilization given by silk.
(nozzle angle)
As shown in Fig. 1～3, Figure 11～16, nozzle angle refers to the surface relative to mother metal 10 and vertical line and welding wire
The angle that the axis of 12 parts finally highlighted from tip 11 is formed.Nozzle angle affects the welding arc heating journey to welding wire
Degree, result is to make welding wire give fluctuation of speed.In detail, if identical welding current, identical nozzle/mother metal spacing
From L, then nozzle angle is that a lean forward side of angle beta (with reference to Fig. 2, Figure 12, Figure 15) compares back rake angle α (with reference to Fig. 1, Figure 11, figure
14), welding wire is given speed and be increased.Therefore, nozzle angle at back rake angle α by the end of the scope of 60 °, the angle beta that leans forward by the end of
It is managed in the range of 60 °, welding wire can be made to give velocity-stabilization, the most preferably.
(the giving speed V:50～120g/min of welding wire)
When giving speed less than 50g/min of welding wire, welding current is too low and electric arc is unstable, is susceptible to lack of penetration.
Therefore, the speed of giving of welding wire is preferably more than 50g/min, more preferably more than 55g/min.On the other hand, if the giving of welding wire
To speed higher than 120g/min, then deposition amount becomes superfluous and is susceptible to heat cracking, it addition, slag fissility also deteriorates.
Therefore, the speed of giving of welding wire is preferably below 120g/min, more preferably below 115g/min.
(speed of welding v:20～60cm/min)
When speed of welding is less than 20cm/min, deposition amount becomes superfluous and is susceptible to heat cracking.Therefore, speed of welding
It is preferably more than 20cm/min, more preferably more than 25cm/min.On the other hand, if speed of welding is higher than 60cm/min, then come
Not as good as supplying melting metal, weld bead shape is unstable and is susceptible to incomplete fusion and slag inclusion.Therefore, speed of welding is preferably
Below 60cm/min, more preferably below 55cm/min.
(deposition amount of per unit weld length: 1.8～4.5g/cm)
The deposition amount of per unit weld length be welding wire give speed/speed of welding.The deposition of per unit weld length
When amount is less than 1.8g/cm, deposition amount is not enough, and weld bead shape is unstable and incomplete fusion and slag inclusion occur.Therefore, per unit welding is long
The deposition amount of degree is preferably more than 1.8g/cm, more preferably more than 2.0g/cm.On the other hand, if per unit weld length molten
Amount of applying is higher than 4.5g/cm, then deposition amount becomes superfluous, and the solidification shrinkage amount of motlten metal is excessive and fusion penetration shape also becomes pears
Shape, the direction that therefore solidification shrinkage occurs is vertical relative to final solidification portion, and heat cracking is susceptible to.Therefore, per unit
The deposition amount of weld length is preferably below 4.5g/cm, more preferably below 4.3g/cm.
Welding current and arc voltage, enter as described welding wire is given a speed controlling means at proper range
Row sum-equal matrix.Power supply characteristic is dropping characteristic, constant-voltage characteristic.Here, so-called dropping characteristic, it is simply that even if arc length becomes
Dynamic, the change of electric current is also few, it is possible to the characteristic of the power supply of stable welding.Specifically, when arc length is long, by temporarily adding
Fast welding wire give speed, arc length in short-term, by slowing down the speed of giving of welding wire, thus keeps making current stabilization unchangeably
Change.Electric power polarity is DCEP (Direct Current Electrode Positive), AC (Alternating Current)
?.
(series connection submerged-arc welding condition)
The bonding layer soldering method of the present invention can also be suitable in series connection welding, is preferably suitable for following condition.Further, nozzle
As shape is welded with monofilament, from the elbow shape shown in the straight tube-like shown in Fig. 4, Fig. 8～10 or Japanese Patent Publication 62-58827
Such shape shown in the Fig.3b of number publication suitably selects.
(nozzle/mother metal spacing)
As shown in Figure 4, as welding with monofilament, nozzle/mother metal spacing is that welding wire 12a (12b) is from tip 11a (11b)
Final distance L between prominent part and mother metal 10, preferably 20～the scope of 40mm.Further, for nozzle/mother metal spacing
For from, it is also possible to backward electrode 11a is different with rear row pole 11b.It addition, the nozzle form of tip 11a, 11b is shown in Fig. 8～10
Elbow shape time nozzle/mother metal spacing as shown in distance L between tip 11 and mother metal 10 in Figure 11～16.Backward electrode
Anode-cathode distance between 11a and rear row pole 11 is preferably 15mm～25mm.As long as in the range of 15mm～25mm, then can obtain
Obtain weld bead shape well.
(nozzle angle)
As shown in Figure 4, as welding with monofilament, nozzle angle is the line vertical relative to the surface of mother metal 10 and welding wire
The angle [alpha] (β) that 12a (12b) is constituted from the axis of part the most prominent for tip 11a (11b).Backward electrode 11a, rear row pole 11b
Nozzle angle (back rake angle α, lean forward angle beta) be all managed in the range of ± 60 ° (back rake angle 60 ° is to top rakes 60 °), this
In order to make welding wire give speed and preferred.Further, when the nozzle form of tip 11a, 11b is the elbow shape shown in Fig. 8～10
Nozzle angle α, β in Figure 11～16 by shown in nozzle angle α, β of tip 11.
(welding wire give speed backward electrode VL: 45～90g/min, rear row pole VT: 60～110g/min)
Welding wire give in speed, backward electrode is less than during 45g/min or rear row is extremely low when 60g/min, welding current mistake
Little and electric arc is unstable, it is susceptible to lack of penetration.On the other hand, if welding wire give in speed, backward electrode higher than 90g/min or
Rear row is high in 110g/min, then deposition amount becomes superfluous and is susceptible to heat cracking, it addition, slag fissility also deteriorates.
Further, in series connection welding, preferably make backward electrode welding wire to give speed slower than rear row.The deposition formed by backward electrode
Amount of metal is less, it is possible to reduce the welding bead degree of depth, increases weld width, it is difficult to heat cracking occurs.Therefore, welding wire is given
For speed, backward electrode is preferably 45～90g/min, rear row is highly preferred be 60～110g/min scope.
(speed of welding v:30～55cm/min)
When speed of welding is less than 30cm/min, deposition amount becomes superfluous, and heat cracking is susceptible to.On the other hand, if welding
Connecing speed and be higher than 55cm/min, then have little time supplying melting metal, weld bead shape is unstable, and incomplete fusion and slag inclusion are susceptible to.
Therefore, speed of welding is preferably the scope of 30～55cm/min.
(deposition amount of per unit weld length: 2.8～3.8g/cm)
The deposition amount of per unit weld length be (welding wire giving speed+rear row pole of the welding wire of backward electrode give speed
Degree)/speed of welding.When the deposition amount of per unit weld length is less than 2.8g/cm, deposition amount is not enough and welding efficiency reduces.Separately
On the one hand, if the deposition amount of per unit weld length is higher than 3.8g/cm, then deposition amount becomes superfluous, and the solidification of motlten metal is received
Contracting amount is excessive and fusion penetration shape becomes pyriform, and the direction that therefore solidification shrinkage occurs vertically and is easily sent out relative to final solidification portion
Raw heat cracking.Therefore, the deposition amount of per unit weld length is preferably the scope of 2.8～3.8g/cm.
As power supply characteristic welds with monofilament, dropping characteristic, constant-voltage characteristic.It addition, polarity is also DCEP, AC
It is suitable for.Alternatively, it is also possible to be applicable to V-arrangement tie lines, Scott tie lines.
The bonding layer soldering method of the present invention is readily adaptable for use in the thickness of slab mother metal less than 150mm.It addition, be not excluded for towards X slope
The application of mouth.When being applied to X groove, in the welding to rear side, as face side, in filler is filled in groove
Carry out bonding layer welding.It addition, after being carried out the second layer after bonding layer welding by the bonding layer soldering method of the present invention, except filling
Agent, can be carried out welding or can also suitable gas protecting with submerged-arc welding as described welding condition or under different condition
Protect the welding method of arc welding etc..
Embodiment
Above, it is set forth for being used for implementing the mode of the present invention, below, will confirm that the reality of the effect of the present invention
The comparative example of the important document executing example and be unsatisfactory for the present invention is contrasted, and specifically illustrates.Further, the present invention is not implemented by this
Example limits, and can also be changed enforcement in the scope shown in technical scheme, and these are all contained in the technical scope of the present invention
In.
(making test body)
The high Cr system CSEF steel of preparation composition as shown in Table 1 is constituted, thickness of slab t is the sheet material of 250mm, is added by machinery
Work, the radius of curvature R of the bottom land forming groove is 10mm, bevel angle θ is the narrow groove of 4 ° and as mother metal (with reference to Fig. 5).
It addition, prepare the shape (metal dust, wire shot) shown in table 4 and the filler of composition, in the groove of mother metal, fill to table
Distribution height h (with reference to Fig. 7) shown in 4.Further, about filler, metal dust is mean diameter 75 μm, and wire shot is string diameter
1mm, Cutting Length 1mm.
Use the granularity shown in the composition shown in table 2 and the welding wire of string diameter 4mm and table 3 and the solder flux of composition, for mother
The groove of material, utilizes front end bent nozzle (with reference to Fig. 8～10) to carry out monolayer single track submerged-arc welding under the following conditions, makes figure
Test body 20 shown in 5.
(welding condition)
Nozzle/mother metal spacing: 30mm
Nozzle angle: 0 °
Electrode characteristic: dropping characteristic
Polarity of electrode: AC monofilament
Welding posture: downwards
Welding current: 400A
Weldingvoltage: 31V
Welding wire give speed: 80g/min
Speed of welding: 40cm/min
The deposition amount of per unit weld length: 2.0g/cm
[table 1]
※ contains inevitable impurity
[table 2]
※ contains inevitable impurity
[table 3]
※ BaO, SrO, Na2O, Li2O, K2O, MnO, FeO, TiO2At least one
(evaluation)
(viability of weld part)
The scope of the 300mm outside initial, the end portion removing weld seam of the test body made, disconnected at every 50mm
Face, by visualization macrostructure, observes with or without weld defect that (slag inclusion, slag fissility, slag burn viscous, incomplete fusion, do not weld
Thoroughly).Further, about slag fissility, with hammer, the solder flux being attached to weld the welding bead surface after terminating is beaten 3 times, molten
Slag be easily peeled off for qualified, unstripped for defective.There is no representing with "○" in table 4 of any weld defect, occur
Weld defect its content is shown in table 4.
After observing described weld defect, visualization weld bead shape.In detail, the evaluation at slag fissility is observed
The appearance of vestige that middle slag is peeled off, weld bead shape stable for qualified, show in table 4 with "○", instability be
Defective, show in table 4 with "×".
(high temperature resistance is anti-thread breakage)
For test body, in the scope of length 300mm of the initial part and end portion removing weld seam, every 50mm cuts off at 5,
Observe the macrostructure of section.5 sections the most do not occur crackle for qualified, show in table 4 with "○", more than 1
Occur crackle for defective, show in table 4 with "×".
[table 4]
As shown in table 4, the distribution height of test body No.1～the composition of filler of 3 and groove is in the scope of the present invention
In, the viability of weld part and high temperature resistance are anti-thread breakage well.
In contrast, test body No.4 is because the C content of filler is superfluous, so the C thickening of welding metal causes high temperature
Crackle occurs.Test material No.5 is because the Si content of filler is superfluous, and test material No.6 is superfluous because of the Mn content of filler, institute
Sticky hair is burnt raw with slag.Test material No.7 is because the P content of filler is superfluous, and test material No.8 is because of the S content mistake of filler
It is surplus, so heat cracking occurs.
Test body No.9 is because the distribution of filler is superfluous, so weld shape is projection welding road, therefore incomplete fusion and
Slag inclusion occurs.Test body No.10 is because the distribution of filler is the most not enough, so the C thickening of metal, high temperature can not be suppressed to weld
Crackle occurs.
The application Japan's patent application based on filing date on July 18th, 2014, with patent application 2014-
The claim of priority of application based on No. 147996.Patent application the 2014-147996th by referring to and enroll this specification.
Symbol description
10 mother metals (welded material)
11 tips
11a backward electrode (tip)
Row pole (tip) after 11b
12,12a, 12b welding wire
20 test body
21 bonding layer welding metals
21f filler
22 welding metals
Claims (13)
1. a bonding layer submerged-arc welding method, it is characterised in that be the bonding layer submerged-arc welding method with high Cr system CSEF steel as mother metal, will
Containing below C:0.10 mass %, below Si:0.50 mass %, below Mn:1.50 mass %, below P:0.025 mass %, S:
Below 0.025 mass %, metal dust that surplus is made up of Fe and inevitable impurity or wire shot, to the slope of described mother metal
Fill in mouthful and weld to distribution height 1.0～4.0mm.
Bonding layer submerged-arc welding method the most according to claim 1, wherein, the welding wire for described welding contain C:0.03～
Below 0.13 mass %, Si:0.05～0.50 mass %, Mn:0.50～2.20 mass %, P:0.015 mass %, S:0.010
Below quality %, Ni: higher than 0.20 mass % and below 1.00 mass %, Cr:8.00～10.50 mass %, Mo:0.20～
1.20 mass %, V:0.05～0.45 mass %, Nb:0.020～0.080 mass %, N:0.02～0.08 mass %, surplus is
Fe and inevitable impurity.
Bonding layer submerged-arc welding method the most according to claim 2, wherein, described welding wire possibly together with from Cu:1.70 mass % with
Under, the group that constituted below B:0.005 mass %, below W:2.0 mass % and below Co:3.0 mass % selects at least
More than one.
4., according to the bonding layer submerged-arc welding method described in Claims 2 or 3, wherein, the solder flux for described welding is expressed from the next
Basicity be 1.0～3.3,
Basicity=(CaF2+CaO+MgO+SrO+Na2O+Li2O+1/2(MnO+FeO))/(SiO2+1/2(Al2O3+TiO2+ZrO2))
Here, each compound represents the mass percentage content of each compound in solder flux gross mass.
Bonding layer submerged-arc welding method the most according to claim 4, wherein, described bonding layer submerged-arc welding method is bonding layer monofilament submerged arc
Soldering method, welds with following condition: making welding wire give speed V is 50～120g/min, and speed of welding v is 20～60cm/
Min, described welding wire deposition amount V/v giving the per unit weld length that the ratio of speed and described speed of welding is tried to achieve is 1.8
～4.5g/cm.
Bonding layer submerged-arc welding method the most according to claim 4, wherein, described bonding layer submerged-arc welding method is bonding layer series connection submerged arc
Soldering method, welds with following condition: make the welding wire of backward electrode give speed VLIt is 45～90g/min, the welding wire of rear row pole
Give speed VTBeing 60～110g/min, speed of welding v is 30～55cm/min, and the deposition amount of per unit weld length is 2.8
～3.8g/cm.
Bonding layer submerged-arc welding method the most according to claim 5, wherein, nozzle/mother metal spacing is 20～40mm.
Bonding layer submerged-arc welding method the most according to claim 7, wherein, in nozzle angle, back rake angle α is the model of 0 ° to 60 °
Enclosing, the angle beta that leans forward is the scope of 0 ° to 60 °.
Bonding layer submerged-arc welding method the most according to claim 8, wherein, nozzle form is straight tube-like or elbow shape.
Bonding layer submerged-arc welding method the most according to claim 6, wherein, nozzle/mother metal spacing is 20～40mm.
11. bonding layer submerged-arc welding methods according to claim 10, wherein, in nozzle angle, back rake angle α is 0 ° to 60 °
Scope, the angle beta that leans forward is the scope of 0 ° to 60 °.
12. bonding layer submerged-arc welding methods according to claim 11, wherein, nozzle form is straight tube-like or elbow shape.
13. series connection bonding layer submerged-arc welding methods according to claim 1, wherein, described bonding layer submerged-arc welding method is bonding layer string
Connection submerged-arc welding method, the anode-cathode distance between backward electrode and rear row pole is 15mm～25mm.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2014147996A JP6282191B2 (en) | 2014-07-18 | 2014-07-18 | First layer submerged arc welding method of high Cr CSEF steel |
| JP2014-147996 | 2014-07-18 | ||
| PCT/JP2015/070436 WO2016010122A1 (en) | 2014-07-18 | 2015-07-16 | FIRST-LAYER SUBMERGED ARC WELDING METHOD FOR HIGH-Cr CSEF STEEL |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN106232287A true CN106232287A (en) | 2016-12-14 |
| CN106232287B CN106232287B (en) | 2019-07-02 |
Family
ID=55078608
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201580022331.8A Expired - Fee Related CN106232287B (en) | 2014-07-18 | 2015-07-16 | The bonding layer submerged arc soldering method of high Cr system CSEF steel |
Country Status (3)
| Country | Link |
|---|---|
| JP (1) | JP6282191B2 (en) |
| CN (1) | CN106232287B (en) |
| WO (1) | WO2016010122A1 (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN107498145A (en) * | 2017-07-27 | 2017-12-22 | 江苏省沙钢钢铁研究院有限公司 | A kind of welding method of heap " submerged-arc welding deposited metal test " transition zone |
| CN107999997A (en) * | 2017-11-23 | 2018-05-08 | 青岛武船重工有限公司 | A kind of FAB methods welding filling powder |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
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| TWI677398B (en) * | 2018-10-24 | 2019-11-21 | 葉均蔚 | Welding method using alloy powder as welding filler material |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN107498145A (en) * | 2017-07-27 | 2017-12-22 | 江苏省沙钢钢铁研究院有限公司 | A kind of welding method of heap " submerged-arc welding deposited metal test " transition zone |
| CN107999997A (en) * | 2017-11-23 | 2018-05-08 | 青岛武船重工有限公司 | A kind of FAB methods welding filling powder |
Also Published As
| Publication number | Publication date |
|---|---|
| JP2016022502A (en) | 2016-02-08 |
| WO2016010122A1 (en) | 2016-01-21 |
| CN106232287B (en) | 2019-07-02 |
| JP6282191B2 (en) | 2018-02-21 |
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