CN106255565B - The monofilament submerged arc soldering method of high Cr system CSEF steel - Google Patents
The monofilament submerged arc soldering method of high Cr system CSEF steel Download PDFInfo
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- CN106255565B CN106255565B CN201580022412.8A CN201580022412A CN106255565B CN 106255565 B CN106255565 B CN 106255565B CN 201580022412 A CN201580022412 A CN 201580022412A CN 106255565 B CN106255565 B CN 106255565B
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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
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- Mechanical Engineering (AREA)
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- Plasma & Fusion (AREA)
- Chemical & Material Sciences (AREA)
- Materials Engineering (AREA)
- Arc Welding In General (AREA)
- Nonmetallic Welding Materials (AREA)
Abstract
There is provided a kind of in the monofilament submerged-arc welding of high Cr system CSEF steel, the viability of weld part and welding operability are excellent, further, it is possible to inhibit the welding method of heat cracking.The monofilament submerged arc soldering method of high Cr system CSEF steel is characterized in that, welded with following condition: so that welding wire is given speed (V) is 50~120g/min, speed of welding (v) is 20~60cm/min, is 1.8~4.5g/cm by the deposition amount (V/v) that the welding wire gives the per unit length that the ratio between speed and the speed of welding acquire.
Description
Technical field
The present invention relates to submerged arc soldering methods, are to be related to high Cr system CSEF (Creep strength- in more detail
Enhanced Ferritic: creep strength enhancing ferrite) steel monofilament submerged arc soldering method.
Background technique
The chemical reaction container (reactor) of thermal power generation boiler and steam turbine, desulfurization and modification (heavy oil decomposition) because
It operates under high temperature and pressure, so applicable is 1.25Cr-0.5Mo steel, 2.25Cr-1.0Mo steel, 2.25Cr- as material
1.0Mo-V steel etc..In recent years, in the effective use and petroleum refining of heavy oil, it is desirable that further high energy efficiency contains 8 matter
The application for measuring the high Cr system CSEF steel of the Cr of % or more 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, the U.S.) specification defined SA387Gr.91,
SA213Gr.T91 etc..
Thermal power generation boiler, steam turbine, reactor are by forging-ring, forge pipe and bending machining steel plate proper combination, welded
And formed.Moreover, forging-ring also will become 150~450mm of plate thickness, maximum outside diameter is less than 7m, total long number~number 10m.As fire
Shielded arc welding, TIG (Tungsten Inert Gas: tungsten can be used in the welding method of power electricity generation boiler, steam turbine, reactor
Pole inert gas-shielded arc welding) weldering, submerged-arc welding.In addition, thermal power generation boiler, steam turbine and reactor, because of welding in structure
Partial ratio is big, so being strongly required the reduction of welding material, the high energy efficiency of welding.
For the reduction of welding material, having keeps groove width narrow, also, use has reduced slope
The method of the narrow groove of bicker degree.In addition, submerged-arc welding is compared with other welding methods due to energy for high energy efficiency
Effect is higher, so being widely used.But in the submerged-arc welding of high Cr system CSEF steel, for heat cracking when welding,
It is unfavorable condition.As the heat cracking inhibited in submerged-arc welding, the technology for the high energy efficiency for realizing welding, disclose following
Such technology.
For example, in patent document 1, a kind of improvement 9Cr-1Mo steel welding wire is disclosed, C, Si containing specified amount,
Mn, Ni, Cr, Mo, V, Nb and N, and with specified amount limitation Mn and Ni total amount, and with specified amount limitation P, S, Cu, Ti, Al,
B, W, Co and O, surplus are made of Fe and inevitable impurity.Moreover, in patent document 1, by make C 0.070~
0.150 mass %, also, P, S are limited in 0.010 mass % hereinafter, to inhibit heat cracking.
It is by following welding wire and weldering in addition, in patent document 2, disclosing a kind of submerged arc soldering method of 9Cr-1Mo steel
The method that agent is combined to be welded, the welding wire contain C, Mn, Cr, Mo, Ni, V, Nb, Al and N of specified amount, also,
Si and O is limited with specified amount, the solder flux contains the CaF of specified amount2, one or both of CaO and MgO, Al22O3And ZrO2
One or both of and Al, also, with specified amount limit SiO2.Moreover, in patent document 2, make C 0.01~
0.15wt%, Al are 0.005~1.5wt%, Si is 0.05wt% welding wire below and SiO2(substantially not for 5wt% or less
Containing Si), CaF2It is combined for the solder flux of 25~70wt%, to inhibit heat cracking.
In addition, in patent document 3, disclosing a kind of narrow groove (groove width with single layer single track welding regulation shape
10~25mm, 15 ° of bevel angle or less) narrow-clearance submerged arc welding method.Moreover, using 2.4~3.2mm φ as leading electrode
Electrode, the electrode of 4.0~4.8mm φ is used as rear row electrode, makes 50~150mm of interelectrode distance, furthermore using spy
It is fixed thus to ensure the viability of welding metal on one side at the sintered flux being grouped as, make to weld efficiency raising on one side, and press down
Preparing high-temp crackle.
Existing technical literature
Patent document
Patent document 1: No. 4476018 bulletins of Japanese Patent No.
Patent document 2: No. 2529843 bulletins of Japanese Patent No.
Patent document 3: Japanese Patent Publication 4-45271 bulletin
Subject to be solved by the invention
But in existing technology, the submerged-arc welding of high Cr system CSEF steel there is a problem of following.
In the improvement 9Cr-1Mo steel welding wire of patent document 1, because gage of wire is the thin footpath welding wire of 2.4mm φ, institute
With electric arc extends insufficient and is easy to happen incomplete fusion, there is the case where weld part that cannot perfect.In addition, if keeping gage of wire thick
Diameter carries out submerged-arc welding to 4.0mm φ, then the carburetting as caused by base material dilution, causes bonding layer to have the feelings that heat cracking occurs
Condition.
In the submerged arc soldering method of the 9Cr-1Mo steel of patent document 2, because welding wire and solder flux are low Si designs, such as
It is preceding described, it is the slab of 450mm and when towards the welding of narrow groove, welding operability, particularly welding bead shape applied to plate thickness
Shape is easy projection welding road, is to have the case where causing incomplete fusion and slag inclusion as a result.That is, the feelings for thering is the viability of weld part to reduce
Condition.
In the narrow-clearance submerged arc welding method of patent document 3, welding wire described in embodiment and base material are mild steel.Here, high
Cr system CSEF steel welding wire is compared with mild steel welding wire, because joule heat is big, deposition amount becomes larger, and has the sensibility of heat cracking
The case where raising.That is, being only difficult in the welding for solving high Cr system CSEF steel in method described in patent document 3 about heat cracking
Project.
In addition, being also possible to not have by the slag that leading electrode is formed because patent document 3 is series electrical arc-welding
It is sufficiently melted by the electrode of rear row, is not suitable for high-precision welding as reactor.In addition, the bonding layer in narrow groove welds
In, dilution caused by base metals is big.Especially in the case where submerged-arc welding, fusion penetration is very deep, and dilution rate is high, therefore by mother
The influence of material ingredient (especially C) and be easy to happen heat cracking.In order to inhibit the heat cracking, base material can be strongly reduced
Dilution, and make welding metal thin-walled.But if carrying out series connection welding, deposited metal amount increases, and welding metal thickens,
Therefore heat cracking is easy to happen.
In general, by improving weld heat input, that is, welding current, arc voltage are improved, speed of welding is reduced, it can
Efficiency is welded to improve.But if improving weld heat input, especially in the case where narrow groove, fusion penetration shape is easy into
Occurrence risk for pyriform, heat cracking improves.Herein become problem heat cracking, be P, S contained in deposited metal,
When the low-melting compound solidification that Si, Nb are formed, in interdendritic, austenite recrystallization cyrystal boundary segregation, along with welding contraction strain
And the so-called heat cracking occurred.Therefore, as the Retraining Measures of heat cracking, the effectively chemical component tune of welding material
It is whole, specifically, with ultra-high purity (EHP:Extra High Purity) melt by the impurity of P, S etc. inhibit 100ppm with
Under.But ultra-high purity is melted due to having to using electron beam melting and dedicated special furnace wall fire proofed wood, so economically
There are difficult points.It is therefore desirable to also be able to suppress the technology of heat cracking generation under general impurity level.
In addition, the main component of welding wire is also the reason of causing heat cracking in the submerged-arc welding of high Cr system CSEF steel.That is,
The solid core welding wire used for submerged arc welding that is made of the same material of high Cr system CSEF steel, with use in the past by 1.25Cr-0.5Mo,
Each solid core welding wire that the same material of 2.25Cr-1Mo, 2.25Cr-1Mo-V steel is constituted compares, and joule heat is high.That is, high Cr system
The solid core welding wire used for submerged arc welding that the same material of CSEF steel is constituted is if it is with identical welding current, then wire melting and deposition amount
It is more.In addition, the solidification shrinkage amount of the deposited metal is than using in the past by 1.25Cr-0.5Mo, 2.25Cr-1Mo, 2.25Cr-
The solid core welding wire that the same material of 1Mo-V steel is constituted it is big.These all make the heat cracking of the submerged-arc welding of high Cr system CSEF steel
Inhibit more difficult.
Summary of the invention
The present invention is formed in view of the foregoing, and project is, provides a kind of monofilament submerged arc in high Cr system CSEF steel
In weldering, the viability and welding operability of weld part are excellent, and are able to suppress the welding method of heat cracking.
Means for solving the problems
It is that the inventors of the present invention concentrate on studies as a result, it has been found that, in the monofilament submerged-arc welding of high Cr system CSEF steel, pass through regulation weldering
Silk gives speed, speed of welding, it further provides that being then able to suppress height by the deposition amount of the calculated per unit length of ratio between two
The generation of anneal crack line.
That is, the monofilament submerged arc soldering method of high Cr system CSEF steel of the invention, which is characterized in that welded with following condition
Connect: so that welding wire is given speed (V) is 50~120g/min, and making speed of welding (v) is 20~60cm/min, is sent according to the welding wire
Deposition amount (V/v) to the per unit length that the ratio between speed and the speed of welding acquire is 1.8~4.5g/cm.
According to such welding method, in monofilament submerged arc soldering method, slag inclusion, incomplete fusion, is not welded at the deterioration of slag fissility
Equal the bad of weld part is inhibited thoroughly, and weld bead shape is also good.In addition, the heat cracking of welding metal is suppressed.
In addition, in the monofilament submerged arc soldering method of high Cr system CSEF steel of the invention, preferably welding wire contain C:0.03~
0.13 mass %, Si:0.05~0.50 mass %, Mn:0.50~2.20 mass %, P:0.015 mass % or less, S:0.010
Quality % or less, Ni: be higher than 0.20 mass % and below 1.00 mass %, mass %, Mo:0.20 of Cr:8.00~10.50~
1.20 mass %, V:0.05~0.45 mass %, Nb:0.020~0.080 mass %, N:0.02~0.08 mass %, surplus are
Fe and inevitable impurity.
According to such welding method, further improve toughness containing specific element in welding wire by making, it in addition can be with
Make creep rupture strength raising etc..
In addition, preferably welding wire is also with Cu:1.70 matter in the monofilament submerged arc soldering method of high Cr system CSEF steel of the invention
Amount % or less, B:0.005 mass % or less, W:2.0 mass % or less, Co:3.0 mass % amount below contain Cu, B, W, Co
In any one more than, surplus is Fe and inevitable impurity.
According to such welding method, further improve toughness containing specific element in welding wire by making, it in addition can be with
Make creep rupture strength raising etc..
In addition, in the monofilament submerged arc soldering method of high Cr system CSEF steel of the invention, the preferred alkali that is expressed from the next of solder flux
Degree 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 indicates the content (quality %) of each compound in solder flux gross mass.
According to such welding method, it is able to suppress the deterioration etc. of the toughness of welding bead appearance, weld bead shape and welding metal.
In addition, distance is 20 between preferred nozzle/base material in the monofilament submerged arc soldering method of high Cr system CSEF steel of the invention
~40mm.
According to such welding method, it can more reliably inhibit the melting loss as caused by the electric arc of nozzle and deposition amount mistake
It is surplus.
In addition, preferred back rake angle α is in nozzle angle in the monofilament submerged arc soldering method of high Cr system CSEF steel of the invention
0 ° to 60 ° of range, the range that top rake β is 0 ° to 60 °.
According to such welding method, more really welding wire can be made to give velocity-stabilization.
In addition, in the monofilament submerged arc soldering method of high Cr system CSEF steel of the invention, nozzle form be preferably straight tube-like or
Elbow shape.
According to such welding method, more reliably ensures giving property of welding wire and stabilized to electric position.
Invention effect
The viability and welding operability of the weld part of the monofilament submerged arc soldering method of high Cr system CSEF steel of the invention are excellent,
And it is able to suppress heat cracking.In addition, welding method of the invention plays excellent effect in bonding layer monofilament submerged-arc welding,
Especially superior effect is played in first of one layer of bonding layer of monofilament submerged-arc welding.
Detailed description of the invention
Fig. 1 is the front view for indicating the state of tip of welding method of the invention.
Fig. 2 is the front view for indicating the state of tip of welding method of the invention.
Fig. 3 is the front view for indicating the state of tip of welding method of the invention.
Fig. 4 is the sectional view of the shape for indicating the narrow groove of welding method of the invention, the stacking main points of welding metal.
Fig. 5 is the front view for indicating the shape of tip of welding method of the invention.
Fig. 6 is the side view of tip shown in fig. 5.
Fig. 7 is the end view drawing of the spray nozzle front end portion side of tip shown in fig. 5.
Fig. 8 is the front view for indicating the state of tip of welding method of the invention.
Fig. 9 is the front view for indicating the state of tip of welding method of the invention.
Figure 10 is the front view for indicating the state of tip of welding method of the invention.
Figure 11 is the front view for indicating the state of tip of welding method of the invention.
Figure 12 is the front view for indicating the state of tip of welding method of the invention.
Figure 13 is the front view for indicating the state of tip of welding method of the invention.
Specific embodiment
Hereinafter, the mode for implementation of the invention is illustrated in detail.
Welding method of the invention is the monofilament submerged arc soldering method of high Cr system CSEF steel.So-called monofilament submerged arc soldering method, example
It as shown in Figures 1 to 3, is the base material 10 constituted for high Cr system CSEF steel, using interior 1 tip 11 for being inserted with welding wire 12 and not
The solder flux of diagram, the method welded with arc welding.Bonding layer especially suitable for such narrow groove shown in Fig. 4 welds, especially
It is first of one layer of bonding layer of welding.
In welding method of the invention, as base material (welded material), using high Cr system CSEF steel as object.In high Cr system
Have various specifications in CSEF steel, for example, SA387Gr.91, Gr.122 of ASTM specification and ASME specification defined, Gr.92,
The X10CrMoVNb9-1 of Gr.911 and SA213Gr.T91, EN specification (European standards: European requirements) defined,
And firepower atomic force generation technology association, civic organization power generation technical standard-firepower equipment technical standard of firepower equipment
Explanation [the 10th chapter weld part]-defined fiery SFVAF28, fire SFVAF29, fire STBA28, fire STPA28, fire SCMV28.
In chemical component as preferred base material, C, Si, Mn, P, S, Ni, Cr, Mo, V, Nb, N containing specified amount are remaining
Amount is Fe and inevitable impurity.Or it can also (1 selected from this 4 kinds of elements Cu, B, W, Co also containing specified amount
Kind or more).
Specifically, containing C:0.07~0.14 mass %, Si:0.50 mass % or less, Mn:0.70 mass % or less,
P:0.025 mass % or less, S:0.015 mass % or less, Ni:0.50 mass % or less, the mass of Cr:8.00~11.50 %,
Mass %, V:0.15 of Mo:0.25~1.10~0.35 mass %, Nb:0.04~0.10 mass %, N:0.03~0.10 matter
% is measured, surplus is Fe and inevitable impurity.Can also also contain Cu:1.70 mass % or less, B:0.060 mass % with
Under, W:2.50 mass % or less, Co:3.0 mass % or less.In addition, inevitably impurity is, for example, Ti, Al etc..
As one of the gimmick for inhibiting heat cracking to occur of one of project of the invention, limitation heat input can be taken in this way
Gimmick.But welding current and arc voltage, the welding surroundings according to the state of work, the point etc. that is powered are different, and welding wire melts
Energy consumed by melting has the tendency that variation.That is, whether heat cracking, which occurs, also can even if being welded with identical heat input
Difference.Therefore, the inventors of the present invention will regulation welding wire give speed, speed of welding, the deposition amount of per unit length.
That is, welding method of the invention is the monofilament submerged arc soldering method of high Cr system CSEF steel, which is characterized in that with following item
Part is welded: so that welding wire is given speed (V) is 50~120g/min, and speed of welding (v) is 20~60cm/min, according to described
The deposition amount (V/v) that welding wire gives the per unit length that the ratio between speed and the speed of welding acquire is 1.8~4.5g/cm.With
Under the numerical definiteness reason of each condition is illustrated.
<welding wire gives speed V:50~120g/min>
If welding wire gives speed lower than 50g/min, welding current is too low, and electric arc is unstable, lack of penetration generation.Another party
Face, if welding wire gives speed higher than 120g/min, deposition amount is excessive, and heat cracking occurs, and slag fissility is also bad
Change.Therefore, it is 50~120g/min that welding wire, which gives speed,.In addition, from the viewpoint of further suppressing lack of penetration generation, welding wire
Giving speed is preferably 55g/min or more, is gone out from the viewpoint for further suppressing the generation of heat cracking, slag fissility deteriorates
Hair, preferably 115g/min or less.In addition, it is controllable that welding wire gives speed for example by adjusting welding current and arc voltage
In proper range.
<speed of welding v:20~60cm/min>
If speed of welding is lower than 20cm/min, deposition amount is excessive, and heat cracking occurs.On the other hand, if speed of welding
Higher than 60cm/min, then not in time, weld bead shape is unstable for the supply of molten metal, and incomplete fusion and slag inclusion occur.Therefore, it welds
Speed is 20~60cm/min.In addition, speed of welding is preferably from the viewpoint of further suppressing heat cracking and occurring
25cm/min or more, from the viewpoint of keeping weld bead shape stable and further suppressing incomplete fusion and slag inclusion, preferably 55cm/
Min or less.In addition, as shown in Figures 1 to 3, so-called speed of welding is movement speed of the tip 11 of bonding machine in welding direction.
<deposition amount V/v:1.8~4.5g/cm of per unit length>
The deposition amount of per unit length is calculated according to speed/speed of welding of giving of welding wire.It is of the invention to be characterized by, just
Locality controls the deposition amount of the per unit length.If the deposition amount of per unit length is lower than 1.8g/cm, deposition amount is very few, weldering
Road shape is unstable, and incomplete fusion and slag inclusion occur.On the other hand, if the deposition amount of per unit length is higher than 4.5g/cm, deposition
Amount is superfluous, therefore the solidification shrinkage amount of welding metal is excessive and fusion penetration shape also becomes pyriform, therefore the side that solidification shrinkage occurs
To be relative to final solidification portion it is vertical, heat cracking occur.Therefore, the deposition amount of per unit length is 1.8~4.5g/cm.
In addition, the deposition amount of per unit length is preferably from the viewpoint of weld bead shape stabilizes and prevents incomplete fusion slag inclusion
2.0g/cm or more, from the viewpoint of further suppressing heat cracking and occurring, preferably 4.3g/cm or less.
Welding method of the invention, other than the regulation of the welding condition, preferably by defined welding wire and defined
Solder flux is applied in combination.Specifically, welding wire contains C, Si, Mn, P, S, Ni, Cr, Mo, V, Nb, N with specified amount, surplus by Fe and
Inevitable impurity is constituted, and has defined string diameter.Additionally, it is preferred that welding wire is not influenced by base material composition, but have base material same
Deng mechanical performance.It therefore, can also be suitable for containing (1 selected from this 4 kinds of elements Cu, B, W, Co with specified amount in welding wire
Kind or more).In addition, solder flux has defined basicity.Hereinafter, being illustrated for welding wire, solder flux.
<welding wire>
Welding wire used in the present invention with specified amount contain mass %, Si:0.05 of C:0.03~0.13~0.50 mass %,
Mass %, the P:0.015 mass of Mn:0.50~2.20 % or less, S:0.010 mass % or less, Ni: be higher than 0.20 mass % and
1.00 mass % or less, mass %, Mo:0.20 of Cr:8.00~10.50~1.20 mass %, V:0.05~0.45 mass %,
The mass of the Nb:0.020~0.080 mass % of %, N:0.02~0.08 is also suitable for containing Cu, B, W, Co (from this 4 kinds with specified amount
1 kind or more selected in element), surplus is Fe and inevitable impurity, and string diameter is preferably 3~5mm φ.Hereinafter, for each
The numerical definiteness reason of composition is illustrated.
(the mass % of C:0.03~0.13)
Various carbonitrides are precipitated in C and N in conjunction with Cr, Mo, W, V, Nb and B together, and having proposes creep rupture strength
High effect.But C content be lower than 0.03 mass % when, cannot get sufficient effect.On the other hand, if excessively containing C,
Specifically, if C content be higher than 0.13 mass %, have heat cracking there is a situation where.Therefore, the C content of welding wire is 0.03
~0.13 mass %.From the viewpoint for further increasing the effect, C content is preferably 0.04 mass % or more.In addition, from into one
From the perspective of step inhibits heat cracking to occur, preferably 0.12 mass % or less.
(the mass % of Si:0.05~0.50)
Si works as deoxidier, improves the effect of the toughness of welding metal with the oxygen amount reduced in deposited metal
Fruit.But Si content be lower than 0.05 mass % when, cannot get sufficient effect.
On the other hand, Si is ferrite generating elements, if excessively containing, specifically, if Si content is higher than 0.50 matter
% is measured, then causes the ferritic residual of the δ-in welding metal, the toughness deterioration of welding metal.Therefore, the Si content of welding wire is
0.05~0.50 mass %.From the viewpoint of further increasing the effect, Si content is preferably more than 0.05 mass %.Separately
Outside, from the viewpoint of deteriorating the toughness for further suppressing welding metal, then preferably 0.48 mass % is hereinafter, more preferably
0.45 mass % or less.
(mass %, Ni of Mn:0.50~2.20: being higher than 0.20 mass % and below 1.00 mass %)
Mn works as deoxidier, has the effect of the oxygen amount reduced in deposited metal and improves toughness.In addition, Mn and
Ni is austenite forming element, all has the effect that toughness caused by inhibiting the ferritic residual of δ-in welding metal deteriorates.
But Mn content cannot get these effects when being lower than 0.50 mass % or when Ni is below 0.20 mass %, welding metal it is tough
Property deterioration.On the other hand, when Mn content is higher than 2.20 mass % or when Ni content is higher than 1.00 mass %, the toughness of welding metal
Deterioration.Therefore, the Mn content of welding wire is 0.50~2.20 mass %, and the Ni content of welding wire is higher than 0.20 mass % and in 1.00 matter
Measure % or less.In addition, when the total content of Mn and Ni is higher than 1.50 mass %, the toughness deterioration of welding metal, and deposited metal
Ac1Transformation temperature reduces, and can not carry out high tempering, not can be carried out the stabilization processes of tissue.Therefore, the total content of Mn and Ni
Preferably 1.50 mass % or less.
From the viewpoint of further increasing the effect, Mn content is preferably 0.55 mass % or more.In addition, from into one
From the perspective of step inhibits the toughness deterioration of welding metal, preferably 2.15 mass % or less.
From the viewpoint of further increasing the effect, Ni content is preferably 0.25 mass % or more, more preferably
0.30 mass % or more.In addition, from the viewpoint of deteriorating the toughness for further suppressing welding metal, preferably less than 0.95 matter
Measure %.
(the mass % of Cr:8.00~10.50)
Cr is the essential element of high Cr system CSEF steel of the welding wire of the invention used as object, is for ensuring that resistance to oxidation
The indispensable element of property, elevated temperature strength.But Cr content be lower than 8.00 mass % when, oxidative resistance and elevated temperature strength are not filled
Point.On the other hand, Cr is ferrite generating elements, if excessively containing, specifically, if Cr content is higher than 10.50 mass %,
Then cause the ferritic residual of δ-, the toughness deterioration of welding metal.Therefore, the Cr content of welding wire is 8.00~10.50 mass %.
Thereby, it is possible to obtain excellent oxidative resistance and elevated temperature strength.From the viewpoint of further increasing the effect, Cr content is excellent
It is selected as 8.05 mass % or more.In addition, from the viewpoint of deteriorating the toughness for further suppressing welding metal, preferably 10.45
Quality % or less.
(the mass % of Mo:0.20~1.20)
Mo is solution strengthening element, has the effect of improving creep rupture strength.But Mo content is lower than 0.20 matter
When measuring %, it cannot get sufficient creep rupture strength.On the other hand, because Mo is ferrite generating elements, if excessively
Contain, specifically, if Mo content is made to be higher than 1.20 mass %, causes the ferritic residual of the δ-in welding metal, weld
The toughness of metal deteriorates.Therefore, the Mo content of welding wire is 0.20~1.20 mass %.From the viewpoint for further increasing the effect
It sets out, Mo content is preferably 0.22 mass % or more.In addition, going out from the viewpoint that the toughness for further suppressing welding metal deteriorates
Hair, preferably 1.18 mass % or less.
(the mass % of V:0.05~0.45)
V is precipitation strength element, has the effect of improving creep rupture strength as Carbonitride Precipitation.But V
When content is lower than 0.05 mass %, it cannot get sufficient creep rupture strength.On the other hand, V is also ferrite generating elements, if
Excessively contain, specifically, if V content is higher than 0.45 mass %, causes the ferritic residual of the δ-in welding metal, weld
Connect the toughness deterioration of metal.Therefore, the V content of welding wire is 0.05~0.45 mass %.From the sight for further increasing the effect
Point sets out, and V content is preferably 0.10 mass % or more.In addition, going out from the viewpoint that the toughness for further suppressing welding metal deteriorates
Hair, preferably 0.40 mass % or less.
(the mass % of Nb:0.020~0.080)
Nb carries out solution strengthening and is precipitated as nitride, contributes to the stabilized element of creep rupture strength.But
When Nb content is lower than 0.020 mass %, it cannot get sufficient creep rupture strength.On the other hand, Nb is also that ferrite generates member
Element specifically, if Nb content is higher than 0.080 mass %, causes the δ-in welding metal ferritic if excessively containing
Residual, the toughness deterioration of welding metal.Therefore, the Nb content of welding wire is 0.020~0.080 mass %.From further increasing
From the perspective of stating effect, Nb content is preferably 0.022 mass % or more.In addition, from the toughness for further suppressing welding metal
From the perspective of deterioration, preferably 0.078 mass % or less.
(P:0.015 mass % or less)
P is the element for improving heat cracking sensibility.If P content is higher than 0.015 mass %, there is heat cracking to occur
Situation.Therefore, the P content of welding wire is limited in 0.015 mass % or less.Go out from the viewpoint that heat cracking occurs is further suppressed
Hair, P content is preferably 0.010 mass % or less.
(S:0.010 mass % or less)
S is the element for improving heat cracking sensibility.If S content is higher than 0.010 mass %, there is heat cracking to occur
Situation.Therefore, the S content of welding wire is limited in 0.010 mass % or less.Go out from the viewpoint that heat cracking occurs is further suppressed
Hair, S content is preferably 0.009 mass % or less.
(the mass % of N:0.02~0.08)
Various carbonitrides are precipitated in N and C in conjunction with Cr, Mo, W, V, Nb and B together, and having proposes creep rupture strength
High effect.But N content be lower than 0.02 mass % when, cannot get sufficient effect.On the other hand, if excessively containing N,
Specifically, if N content is higher than 0.08 mass %, the deterioration of slag fissility.Therefore, the N content of welding wire is 0.02~0.08
Quality %.From the viewpoint of further increasing creep rupture strength, N content is preferably 0.03 mass % or more.In addition, from molten
From the perspective of slag fissility improves, preferably 0.07 mass % or less.
As that can also be suitable for the ingredient contained with specified amount, illustrate the numerical definiteness reason of Cu, B, W, Co.
(Cu:1.70 mass % or less)
Cu is austenite forming element, and there is toughness caused by inhibiting the ferritic residual of δ-in welding metal to deteriorate
Effect, therefore can also contain.On the other hand, superfluous containing then there is the case where causing heat cracking.Therefore, Cu is 1.70 matter
Measure % or less.The preferred upper limit of Cu is 1.0 mass %, and the preferred upper limit is 0.5 mass %.Cu's contains method, can also
With to the plating of welding wire surface.
(B:0.005 mass % or less)
B, containing carbide dispersion stability is made, has the effect of raising creep rupture strength by micro, therefore
It can contain.On the other hand, superfluous containing then there is the case where causing heat cracking.Therefore, B is 0.005 mass % or less.B
The preferred upper limit be 0.003 mass %, the preferred upper limit be 0.0015 mass %.
(W:2.0 mass % or less)
W is precipitated by the solution strengthening of matrix and fine carbide, and the stabilized member of creep rupture strength is facilitated
Element, therefore can also contain.On the other hand, δ-iron can be caused so superfluous contains due to W and ferrite generating elements
The deterioration of toughness caused by the residual of ferritic.Therefore, W is 2.0 mass % or less.The preferred upper limit of W is 1.8 mass %, more excellent
The upper limit of choosing is 1.7 mass %.
(Co:3.0 mass % or less)
Co is the remaining element for inhibiting delta ferrite, therefore can also be contained.On the other hand, it if surplus contains, reduces
Ac1Point, therefore high tempering can not be implemented, it not can be carried out the stabilization processes of tissue.Therefore Co is set as 3.0 mass % or less.Co
Preferred upper limit be 2.0 mass %, the preferred upper limit is 1.8 mass %.
(surplus: Fe and inevitable impurity)
The surplus of the ingredient of welding wire is Fe and inevitable impurity.As inevitable impurity, for example, can enumerate Ti,
Al etc..
(string diameter of welding wire)
Preferably 3~the 5mm of string diameter used in present invention φ.When string diameter is lower than 3mm φ, sufficient deposition amount cannot be obtained,
Welding efficiency can be sacrificed.On the other hand, if being higher than 5mm φ, even if the design of the welding condition is realized, because of deposition amount
More, heat cracking cannot be inhibited the phenomenon that by still having.
<solder flux>
It is preferred that the basicity of solder flux used in the present invention being expressed from the next 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 indicates the content (quality %) of each compound in solder flux gross mass.
When the basicity of solder flux is lower than 1.0, the oxygen amount in welding metal does not reduce sufficiently and is low tenacity.On the other hand, if
Basicity is higher than 3.3, then welding bead appearance and weld bead shape deterioration.Therefore, in the range of basicity is 1.0~3.3.From further suppressing
From the perspective of the toughness deterioration of welding metal, basicity is preferably 1.3 or more.In addition, from welding bead appearance and weldering is further suppressed
From the perspective of road shape deterioration, preferably 3.2 or less.
In addition, if basicity meets the range, constituting compound of solder flux etc. as solder flux used in the present invention
Other conditions do not have special provision.
Welding method of the invention, other than the welding condition, distance, nozzle shape preferably between regulation nozzle/base material
Shape, nozzle angle.
<distance between nozzle/base material>
As previously mentioned, with high Cr system CSEF steel be same material solid core welding wire used for submerged arc welding, compared to 1.25Cr-
For 0.5Mo, 2.25Cr-1Mo, 2.25Cr-1Mo-V steel is the solid core welding wires of same material, resistance is high, therefore joule heat amount
Greatly, deposition amount is more.Even if that is, with high Cr system CSEF steel be same material welding wire under identical welding current, deposition amount
More, heat cracking is easy to happen.Moreover, Fig. 1~3, Fig. 8~10, shown in Figure 11~13 between tip 11 and base material 10 away from
From longer, joule heat amount is bigger.Therefore, in order to further suppress the generation of heat cracking, preferably by distance between nozzle/base material
L management is 20~40mm.When distance L is lower than 20mm between nozzle/base material, spray nozzle front end portion 11a has by the risk of electric arc melting loss.
If distance L is higher than 40mm between nozzle/base material, deposition amount is superfluous.In addition, from spray nozzle front end portion 11a melting loss is further suppressed
Viewpoint is set out, and distance L is preferably 25mm or more between nozzle/base material, from the viewpoint of further suppressing deposition amount surplus, preferably
For 35mm or less.
Here, distance is that welding wire 12 exposes from spray nozzle front end portion 11a between nozzle/base material as shown in Fig. 1~3, Fig. 8~13
Point and base material 10 between vertical range L.
<nozzle form>
Nozzle form is that such elbow shape shown in such straight tube-like, Fig. 5~7 shown in Fig. 1~3 or Japan are special public
Such shape shown in the Fig.3b of clear 62-58827 bulletin is ok, from ensuring giving property of welding wire and to the stabilized sight of electric position
It is suitable for selection that point, which sets out,.Especially shown in Fig. 5~7 it is such, spray nozzle front end portion 11a is curved in the range of not hindering welding wire to give
Bent elbow shape nozzle makes to stabilize to electric position, the result is that welding wire gives velocity-stabilization.
<nozzle angle>
As shown in Fig. 1~3, Fig. 8~10, Figure 11~13, nozzle angle be the line vertical relative to the surface of base material 10, with
The angle that welding wire 12 is finally constituted from the part outstanding of tip 11, that is, spray nozzle front end portion 11a axis.Moreover, nozzle angle influences
Welding arc is to the degree of heat of welding wire, the result is that welding wire is made to give fluctuation of speed.Specifically, if it is identical welding electricity
Distance L between stream, identical nozzle base material, then nozzle angle is that a side of top rake β (referring to Fig. 2, Fig. 9, Figure 12) compares hypsokinesis
Angle α (referring to Fig.1, Fig. 8, Figure 11), welding wire is given speed and be increased.
Therefore, nozzle angle preferably after range of the inclination alpha until 60 °, top rake β until 60 ° in the range of manage
Reason, this is to make welding wire give velocity-stabilization.
So-called top rake, such as Fig. 2, Fig. 9 and Figure 12, exactly from spray nozzle front end portion 11a expose welding wire light draw one with
The vertical line of sealing wire, relative to the vertical line, when tilting welding wire with the direction of travel of welding on the contrary and weld, welding wire with
The angle that vertical line is constituted.
So-called back rake angle, such as Fig. 1, Fig. 8 and Figure 11, exactly from spray nozzle front end portion 11a expose welding wire light draw one with
The vertical line of sealing wire, relative to the vertical line, when tilting welding wire along the direction of travel of welding and welded, welding wire with
The angle that vertical line is constituted.
Next, for the power supply characteristic of welding method of the invention, electric power polarity, base material plate thickness, base material bevel shape
It is illustrated.
Power supply characteristic is dropping characteristic, constant-voltage characteristic.Here, so-called dropping characteristic, is exactly to become even if arc length
Dynamic, the variation of electric current is also few, can stablize the characteristic of the power supply of welding.Specifically, when arc length is long, by temporarily adding
Fast welding wire gives speed, and arc length gives speed in short-term, by slow down welding wire, so that electric current be made to stablize with remaining unchanged
Change.Electric power polarity is DCEP (Direct Current Electrode Positive), AC (Alternating Current)
?.
Welding method of the invention is with such as aforementioned using thermal power generation boiler, steam turbine and reactor as suitable welding pair
As.Therefore, base material plate thickness is preferably 150~450mm.But welding method of the invention can also be lower than towards base material plate thickness
The welding application of 150mm.Equally, in welding method of the invention, as base material bevel shape, with such narrow slope shown in Fig. 4
Mouth is as suitable welding object.But welding method of the invention is readily applicable to V groove (not shown), X groove.
Welding method of the invention is only to be buried using the bonding layer monofilament of bonding layer 21 shown in Fig. 4 as suitable welding object
Arc welding method.But welding method of the invention is for (not shown) but not only there was only bonding layer 21, but in bonding layer 21
On be also laminated with welding metal, until end layer (top layer) when being welded, can also be applied.In addition, welding of the invention
Method is readily applicable to the series connection submerged-arc welding (not shown) based on V-arrangement tie lines, Scott tie lines.
Embodiment
Hereinafter, the embodiment (No.1~8) for being included in the scope of the present invention and its effect are departed from the scope of the present invention
Comparative example (No.9~14) makes a comparison description.
Prepare the base material of chemical component shown in 3 kinds of tables 1.For the base material, as shown in figure 4, being formed by machining
Plate thickness t is 250mm, and the radius of curvature R of slot bottom is 10mm, and the narrow groove that bevel angle θ is 4 ° is as test body 20.
In addition, preparing the welding wire of chemical component shown in 3 kinds of tables 2.String diameter is 4.0mm φ.Include in welding wire shown in table 2
The Cu of 0.01 mass % contained as inevitable impurity.In addition, using granularity shown in 3 kinds of tables 3, chemical component,
The solder flux of basicity.
[table 1]
[table 2]
[table 3]
Then, in the narrow groove of test body 20 shown in Fig. 4, using solder flux described in welding wire described in table 2 and table 3,
So that welding wire is given speed and speed of welding variation, implements submerged-arc welding.Welding wire gives speed by becoming welding current, speed of welding
Change to be controlled.
Welding condition is as follows.In addition, other conditions are shown in table 4.In addition, being unsatisfactory for the scope of the present invention in table
Content, logarithm draw underscore expression.
(welding condition)
String diameter: 4mm φ
Tip: front end bent nozzle shown in Fig. 8~10 (elbow shape nozzle)
Electrode characteristic: dropping characteristic
Polarity of electrode: AC monopole
Weld posture: downwards
Laminating method: bonding layer single layer single track
For having carried out the test body 20 of the welding, the viability, resistant to high temperatures anti-thread breakage of weld part is evaluated.It is as the result is shown
In table 4.
(viability of weld part)
After welding, visually and in the initial part and end portion for removing weld seam (specifically, refer respectively to away from weldering
The end 100mm of seam.It is same as below.) other than 300mm in the range of every 50mm section observe macrostructure, confirmation whether there is or not
Welding defect (slag inclusion, slag fissility, incomplete fusion, lack of penetration etc.).Not having the case where welding defect is zero (good), there is welding
The case where defect is × (bad).In addition, about slag fissility, with hammer for being attached to welding after welding bead surface
Solder flux beat 3 times, zero (good) is determined as when slag is easily peeled off, × (bad) is determined as when unstripped.
After welding, by visual observation, confirmed also for weld bead shape.Specifically, in the slag fissility
Evaluation in, by visual observation confirmation removing slag after appearance, weld bead shape stablize when be determined as zero (good), welding bead
It is determined as × (bad) when shape is unstable.
(resistant to high temperatures anti-thread breakage)
In the range of the 300mm except the initial part and end portion for removing weld seam, macroscopic view is observed in the section of every 50mm
Tissue.In total 5 sections, there is no being determined as zero (good) when heat cracking, when generation heat cracking is determined as ×
(bad).
[table 4]
As shown in table 4, No.1~8 meet the scope of the present invention, the viability of weld part, resistant to high temperatures anti-thread breakage excellent.
The welding wire of No.9 gives speed beyond lower limit of the invention.In No.9, because welding current is small, welding wire gives speed
It is small, so electric arc is unstable, occur on the boundary of groove face and welding bead lack of penetration.The viability of the weld part of No.9 is poor.
The welding wire of No.10 gives speed beyond the upper limit of the invention.In No.10, because welding current is big, welding wire gives speed
Degree is big, so deposition amount excessively heat cracking generation, and slag fissility also reduces.The viability of the weld part of No.10,
Anti-thread breakage difference resistant to high temperatures.
The speed of welding of No.11 exceeds lower limit of the invention, and the deposition amount of per unit length also exceeds the upper limit of the invention.
In No.11, because speed of welding is slow, deposition amount is excessive and heat cracking occurs.The anti-thread breakage difference resistant to high temperatures of No.11.
The speed of welding of No.12 exceeds the upper limit of the invention.In No.12, welding wire gives (supply of welding metal)
It is unable to catch up with speed of welding, weld bead shape is unstable, and incomplete fusion and slag inclusion has occurred.The viability of the weld part of No.12 is poor.
The deposition amount of the per unit length of No.13 exceeds lower limit of the invention.The deposition amount of No.13 is very few, weld bead shape
It is unstable and incomplete fusion and slag inclusion has occurred.The viability of the weld part of No.13 is poor.
The deposition amount of the per unit length of No.14 exceeds the upper limit of the invention.In No.14, deposition amount is superfluous, therefore welds
The solidification shrinkage amount of metal is excessive and fusion penetration shape also resembles a pear in shape, and heat cracking occurs.The anti-thread breakage difference resistant to high temperatures of No.14.
More than, embodiments and examples, which are described in detail, to be shown for the present invention, but purport of the invention is not
It is limited by the content, interest field must be based on the description broad interpretation of the range of technical solution.In addition, of the invention is interior
Holding can certainly carry out changing change etc. extensively based on foregoing description.
The application is with the Japanese Patent Application for taking the applying date as on July 18th, 2014, patent application 2014-
The preference applied based on No. 147994 advocates, patent application the 2014-147994th by referring to and introduce this specification.
Symbol description
10 base materials (welded material)
11 tips
12 welding wires
20 test body
21 bonding layers
Claims (5)
1. a kind of monofilament submerged arc soldering method of high Cr system CSEF steel, which is characterized in that welded with following condition: sending welding wire
It is 50~120g/min to speed V, speed of welding v is 20~60cm/min, gives speed and welding speed by the welding wire
The deposition amount V/v for the per unit length that the ratio between degree acquires is 1.8~4.5g/cm,
Wherein, welding wire contain mass %, Si:0.05 of C:0.03~0.13~0.50 mass %, Mn:0.50~2.20 mass %,
P:0.015 mass % or less, S:0.010 mass % or less, Ni: it is 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 matter
The mass % of %, N:0.02~0.08 is measured, surplus is Fe and inevitable impurity, and the diameter of the welding wire is 3~5mm,
Also, the basicity that solder flux is expressed from the next 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 indicates the mass percentage content of each compound in solder flux gross mass.
2. the monofilament submerged arc soldering method of high Cr system CSEF steel according to claim 1, wherein the welding wire is also with Cu:
1.70 mass % or less, B:0.005 mass % or less, W:2.0 mass % or less, Co:3.0 mass % amount below contain Cu,
B, more than any one in W, Co, surplus is Fe and inevitable impurity.
3. the monofilament submerged arc soldering method of high Cr system CSEF steel according to claim 1, wherein distance is between nozzle/base material
20~40mm.
4. the monofilament submerged arc soldering method of high Cr system CSEF steel according to claim 3, wherein in nozzle angle, back rake angle α
In 0 ° to 60 ° of range, range of the top rake β at 0 ° to 60 °.
5. the monofilament submerged arc soldering method of high Cr system CSEF steel according to claim 4, wherein nozzle form be straight tube-like or
Elbow shape.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2014147994A JP6290023B2 (en) | 2014-07-18 | 2014-07-18 | Single submerged arc welding method for high Cr system CSEF steel |
| JP2014-147994 | 2014-07-18 | ||
| PCT/JP2015/069560 WO2016009903A1 (en) | 2014-07-18 | 2015-07-07 | Single submerged arc welding method for high chromium csef steel |
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| CN106255565A CN106255565A (en) | 2016-12-21 |
| CN106255565B true CN106255565B (en) | 2019-06-07 |
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| CN201580022412.8A Active CN106255565B (en) | 2014-07-18 | 2015-07-07 | The monofilament submerged arc soldering method of high Cr system CSEF steel |
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| JP (1) | JP6290023B2 (en) |
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| CN110788517A (en) * | 2019-11-05 | 2020-02-14 | 上海欣冈贸易有限公司 | Steel alloy for welding material |
| CN113414519B (en) * | 2021-08-06 | 2022-11-29 | 四川大西洋焊接材料股份有限公司 | ENi6620 nickel-based welding rod for alternating current and preparation method and welding method thereof |
| WO2023037921A1 (en) * | 2021-09-07 | 2023-03-16 | 株式会社神戸製鋼所 | Bond flux for submerged arc welding, and weld metal |
| JP2023038836A (en) * | 2021-09-07 | 2023-03-17 | 株式会社神戸製鋼所 | Bond flux for submerged arc welding and weld metal |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1727108A (en) * | 2004-05-18 | 2006-02-01 | 株式会社神户制钢所 | Welding wire for modified 9Cr-1Mo steel, and submerged-arc welding material |
| CN101015887A (en) * | 2007-01-30 | 2007-08-15 | 山东大学 | Filling metallic particles for overlay welding and its preparation method |
| CN102152020A (en) * | 2011-01-31 | 2011-08-17 | 山东博润工业技术有限公司 | Coating powder for submerged arc surfacing of low-carbon steel and application method thereof |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH03281066A (en) * | 1990-03-28 | 1991-12-11 | Nippon Steel Corp | Square groove one-side welding method |
| JP2877625B2 (en) * | 1992-08-17 | 1999-03-31 | 川崎製鉄株式会社 | Groove shape detector in submerged arc welding of thick steel plate |
| JP3017058B2 (en) * | 1995-09-29 | 2000-03-06 | 株式会社神戸製鋼所 | Cut wire for welding |
| KR100811920B1 (en) * | 2007-02-07 | 2008-03-10 | 대우조선해양 주식회사 | One side welding method of butt-welded joints |
| JP2011131243A (en) * | 2009-12-24 | 2011-07-07 | Nippon Steel Corp | Arc welding method and arc weld joint of galvanized steel plate |
| JP5987737B2 (en) * | 2012-04-09 | 2016-09-07 | Ｊｆｅスチール株式会社 | Narrow groove welding method for steel |
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2014
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- 2015-07-07 CN CN201580022412.8A patent/CN106255565B/en active Active
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Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1727108A (en) * | 2004-05-18 | 2006-02-01 | 株式会社神户制钢所 | Welding wire for modified 9Cr-1Mo steel, and submerged-arc welding material |
| CN101015887A (en) * | 2007-01-30 | 2007-08-15 | 山东大学 | Filling metallic particles for overlay welding and its preparation method |
| CN102152020A (en) * | 2011-01-31 | 2011-08-17 | 山东博润工业技术有限公司 | Coating powder for submerged arc surfacing of low-carbon steel and application method thereof |
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| JP2016022500A (en) | 2016-02-08 |
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| CN106255565A (en) | 2016-12-21 |
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