KR101760828B1 - Ni-BASE FLUX CORED WIRE WELDING CONSUMABLE - Google Patents
Ni-BASE FLUX CORED WIRE WELDING CONSUMABLE Download PDFInfo
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- KR101760828B1 KR101760828B1 KR1020150116000A KR20150116000A KR101760828B1 KR 101760828 B1 KR101760828 B1 KR 101760828B1 KR 1020150116000 A KR1020150116000 A KR 1020150116000A KR 20150116000 A KR20150116000 A KR 20150116000A KR 101760828 B1 KR101760828 B1 KR 101760828B1
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
- B23K35/22—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
- B23K35/3033—Ni as the principal constituent
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
- B23K35/02—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by mechanical features, e.g. shape
- B23K35/0255—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by mechanical features, e.g. shape for use in welding
- B23K35/0261—Rods, electrodes, wires
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
- B23K35/02—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by mechanical features, e.g. shape
- B23K35/0255—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by mechanical features, e.g. shape for use in welding
- B23K35/0261—Rods, electrodes, wires
- B23K35/0266—Rods, electrodes, wires flux-cored
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- 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
- B23K35/3033—Ni as the principal constituent
- B23K35/304—Ni as the principal constituent with Cr as the next major constituent
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
- C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
- C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
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- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Chemical & Material Sciences (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Nonmetallic Welding Materials (AREA)
Abstract
A Ni-based flux cored wire welding material according to an aspect of the present invention is a welding material comprising a core and an enclosure enclosing the core, wherein processing in the form of a flux cored wire is achieved by optimizing the alloy composition of the welding material and the sheath surrounding the core It is easy to use, has excellent physical properties and can be welded electronically.
Description
The present invention relates to a Ni-based flux cored wire welding material.
In the 20th century, super-heat-resistant alloys have been widely used as basic structural materials in the aerospace industry, nuclear power industry, power plant industry, and petrochemical industry. Among them, Ni base alloy is precipitation hardening type alloy using precipitation phenomenon of austenite phase with FCC, and has the best performance among super heat resistant alloys. It is a high temperature and high stressed material such as blades, disks and combustion chamber of gas turbine They are widely used as structural materials for major parts. And it has quality and strong property even at the temperature of 980 ℃ or more, especially it is resistant to oxidation, corrosion and strong in phosphoric acid solution. Therefore, it is used in piping and valve equipment for chemical and pollution prevention facilities. Among many Ni base alloys, Inconel 625 alloy (Ni-Cr-Mo-Nb alloy) has excellent weldability. The welding technique used is mainly GTAW (Gas Tungsten Arc Welding), SMAW (Shielded Metal Arc Welding) Arc Welding, Submerged Arc Welding (SAW), and Flux-Cored Arc Welding (FCAW). In the case of FCAW welding technique, there has been no progress in the development of welding materials in Korea, and some welding material makers have been developing and selling FCAW welding materials. However, the above welding materials can not be welded electronically. Fillet welding was only possible in the viewing posture.
Thus, the development of welding materials for FCAW is late compared to other welding materials, and recently, welding materials capable of attaining vertical-up welding postures have been developed and are being used more and more frequently.
Inconel 625 alloy flux cored wire which is currently sold domestically and abroad is composed of products which are sold using Inconel 625 sheath, and she uses Inconel 625 sheath which controls some Fe content.
When using the Inconel 625 sheath, it is difficult to process as a flux cored wire because of the high tensile strength of the sheath of the wire and the high degree of work hardening compared to the generally used carbon steel and stainless steel sheaths. Also, the electric resistance is 1.5 to 10 times higher than that of carbon steel and stainless steel, which makes it difficult to control current and obtain easy arcability.
Therefore, it is desired to develop Ni-based flux cored wire welding material that can be preferably applied to Inconel 625 alloy among Ni-base alloys, easy to process in the form of flux cored wire, and capable of electron weldability.
One aspect of the present invention is to provide a Ni-based flux cored wire welding material that is easy to process in the form of flux cored wire and has excellent physical properties and electron weldability by optimizing alloy composition of the welding material and the alloy composition of the sheath surrounding the core .
On the other hand, the object of the present invention is not limited to the above description. It will be understood by those of ordinary skill in the art that there is no difficulty in understanding the additional problems of the present invention.
A Ni-based flux cored wire welding material according to an aspect of the present invention is a welding material comprising a core and a shell surrounding the core,
The welding material according to claim 1, wherein the welding material comprises 0.01 to 0.1% of C, 0.1 to 1.0% of Si, 0.01 to 1.0% of Mn, less than 0.035% of P and S, 18.0 to 25.0% of Cr, At least one of K, Na, and Li, and at least one of K, Na, and Li, and at least one of K, Na, and Li is contained in an amount of 7.0 to 11.0%, Ti of 0.01 to 1.0%, Nb of 3.0 to 4.5%, Fe of 0.01 to 5%, TiO2 of 3.5 to 15% : 0.05 to 1.5%, at least one of F and Ca: 0.05 to 1.0%, at least one of Al and Mg: 0.1 to 1.5%, remaining Ni and other unavoidable impurities,
Wherein the shell is composed of 0.01 to 0.1% of C, 0.1 to 1.0% of Si, 0.01 to 1.0% of Mn, 18.0 to 25.0% of Cr, 0.01 to 1.0% of Ti, 0.01 to 1.0% of Ti, : 1.0% or less, and the remaining Ni.
In addition, the solution of the above-mentioned problems does not list all the features of the present invention. The various features of the present invention and the advantages and effects thereof will be more fully understood by reference to the following specific embodiments.
The Ni-based flux cored wire welding material according to one aspect of the present invention can be easily processed in the form of flux cored wire by optimizing the alloy composition of the welding material and the sheath surrounding the core, and is excellent in physical properties and can be welded electronically The effect is excellent.
In addition, it has an effect of securing good physical properties such as tensile strength and elongation at high temperature while exhibiting good weldability.
Hereinafter, preferred embodiments of the present invention will be described. However, the embodiments of the present invention can be modified into various other forms, and the scope of the present invention is not limited to the embodiments described below. Further, the embodiments of the present invention are provided to more fully explain the present invention to those skilled in the art.
Inconel 625 alloy Flux Cored Wire, currently sold domestically and internationally, is made of Inconel 625 sheath. Most of the products are made of Inconel 625 sheath. Inconel 625 outer sheath, which controls some Fe content, is used.
When using Inconel 625 sheath, it is difficult to process as flux cored wire because of high tensile strength of wire and high working hardness compared to carbon steel and stainless steel which are widely used. Also, the electric resistance is 1.5 to 10 times higher than that of carbon steel and stainless steel, which makes it difficult to control current and obtain easy arcability.
Therefore, the present invention controls the alloy composition of Inconel 625 compared to Inconel 625 to ensure proper tensile strength and machining characteristics by using a Ni-based sheath whose alloy content is minimized and solve the existing problems by using a material having good electric resistance characteristics Respectively.
Hereinafter, the Ni-based flux cored wire welding material according to one aspect of the present invention will be described in detail.
A Ni-based flux cored wire welding material according to an aspect of the present invention is a welding material comprising a core and a shell surrounding the core,
The welding material according to claim 1, wherein the welding material comprises 0.01 to 0.1% of C, 0.1 to 1.0% of Si, 0.01 to 1.0% of Mn, less than 0.035% of P and S, 18.0 to 25.0% of Cr, At least one of K, Na, and Li, and at least one of K, Na, and Li, and at least one of K, Na, and Li is contained in an amount of 7.0 to 11.0%, Ti of 0.01 to 1.0%, Nb of 3.0 to 4.5%, Fe of 0.01 to 5%, TiO2 of 3.5 to 15% : 0.05 to 1.5%, at least one of F and Ca: 0.05 to 1.0%, at least one of Al and Mg: 0.1 to 1.5%, remaining Ni and other unavoidable impurities,
Wherein the shell is composed of 0.01 to 0.1% of C, 0.1 to 1.0% of Si, 0.01 to 1.0% of Mn, 18.0 to 25.0% of Cr, 0.01 to 1.0% of Ti, 0.01 to 1.0% of Ti, : 1.0% or less, and the remaining Ni.
The Ni-based flux cored wire welding material according to one aspect of the present invention preferably includes the following composition with respect to the total weight including the core and the outer shell surrounding the core. In the following, the content of each composition means weight%, unless otherwise specified.
C: 0.01 to 0.1%
Carbon (C) is a component that combines with chromium (Cr) to form chromium carbide and improve strength and hardness. If the content of C is less than 0.01%, the formation of chromium carbide is inadequate and the strength can not be secured. On the other hand, when the content of C is more than 0.1%, excess carbide is formed and the crack resistance is lowered, There is a problem in that the occurrence of the problem is increased.
Therefore, in the present invention, the content of C is preferably limited to 0.01 to 0.1%.
Si: 0.1 to 1.0%
Silicon (Si) is a component that improves deoxidation and workability (spreadability). When the content is less than 0.1%, deoxidization power is insufficient and bead spreadability is lowered. On the other hand, when the content exceeds 1.0% , There is a problem that the generation of Laves phase increases and the fraction of the low melting point compound increases, thereby increasing the crack susceptibility.
Therefore, in the present invention, the content of Si is preferably limited to 0.1 to 1.0%. More preferably, it is 0.1 to 0.5%.
Mn: 0.01 to 1.0%
Manganese (Mn) is a component that improves slag fluidity and improves bead shape, and maintains the proper strength and toughness of the weld. In order to obtain the above-mentioned effect, it is necessary to contain Mn at not less than 0.01%, but if the content exceeds 1.0%, rapid decrease in toughness may be caused, which is not preferable.
Therefore, in the present invention, the content of Mn is preferably limited to 0.01 to 1.0%. More preferably, it is 0.01 to 0.5%.
At least one of P and S: less than 0.035% in total
P and S are one of the major elements affecting high-temperature cracking, and can generate hot cracks by generating Ni alloys such as Ni3S7, NiS, and Ni3P and low melting point compounds. Therefore, P and S impurity control is essentially necessary, and the total content of P and S can be controlled to reduce the occurrence of hot cracks. Therefore, it is preferable that at least one of P and S is less than 0.035% in total.
Cr: 18.0 to 25.0%
Chromium (Cr) is an element that increases hardness by bonding with carbon (C) to form carbide and increases corrosion resistance. If the content of Cr is less than 18%, it is difficult to secure sufficient corrosion resistance and the above-mentioned effect is difficult to expect. On the other hand, when the content exceeds 25%, chromium carbide is excessively formed and toughness is deteriorated.
Therefore, in the present invention, the content of Cr is preferably limited to 18.0 to 25.0%. And more preferably 20.0 to 23.0%.
Mo: 7.0 to 11.0%
Molybdenum (Mo) is a component that forms a carbide by bonding with carbon (C), and is a component that plays a favorable role in abrasion resistance, hardness and corrosion resistance. If the content of Mo is less than 7.0%, it is difficult to expect the above-mentioned effect. On the other hand, when the content of Mo exceeds 11.0%, the Mo is precipitated into Laves and the crack resistance is lowered.
Therefore, in the present invention, it is preferable to limit the Mo content to 7.0 to 11.0%. More preferably, it is 8.0 to 10.0%.
Ti: 0.01 to 1.0%
Ti can increase precipitation hardening effect in Ni-based alloys.
When the content is less than 0.01%, the above effect is not sufficient. On the other hand, when the content exceeds 1.0%, a compound such as Ni3Ti, Ni3 (Ti, Al) is formed and it is difficult to secure a good welded portion due to the occurrence of strain-age-crack.
Therefore, in the present invention, the content of Ti is preferably limited to 0.01 to 1.0%. More preferably, it is 0.01 to 0.4%.
Nb: 3.0 to 4.5%
Niobium (Nb) is an element that forms carbides, nitrides, and carbonitrides by bonding with carbon or nitrogen, and is an element that precipitates Ni and Ni3Nb and exhibits remarkable precipitation strengthening effect. In order to obtain the above-mentioned effect, it is necessary to contain Nb at 3.0% or more. However, when the content exceeds 4.5%, precipitation in the Laves Phase causes a problem of lowering the crack resistance.
Therefore, in the present invention, it is preferable to limit the content of Nb to 3.0 to 4.5%. More preferably, it is 3.15 to 4.15%.
Fe: 0.01 to 5.0%
Iron (Fe) is an element that is indispensably contained in a welding material or a base material in a Ni-based alloy. If the content exceeds 5.0%, it may be vulnerable to cracks due to an increase in formation of the Laves phase, and it is desirable to minimize the corrosion resistance because it may reduce the corrosion resistance. However, it is preferable that the content of Fe is limited to 0.01 to 5.0% because the cost is excessively consumed if it is controlled to less than 0.01%.
TiO2 (titanium dioxide): 3.5 to 15.0%
The TiO2 serves as a slag forming agent and functions to prevent the liquid weld metal from solidifying and allowing the liquid weld metal to flow down before it coagulates. In order to exhibit such an effect, it is preferable to add 3.5% or more in the present invention. However, when the content exceeds 15.0%, the oxide content in the weld metal increases sharply, and the impact resistance at cryogenic temperature is lowered, and it is difficult to secure electron weldability due to excessive slag content. Therefore, the content of TiO2 is preferably limited to 3.5-15.0%.
SiO2 (silicon dioxide): 0.3 to 3.0%
The SiO2 serves as a slag forming agent to increase the flowability of weld slag and weld bead spreadability. In order to exhibit such an effect, it is preferable to add at least 0.3% in the present invention. However, when the content exceeds 3.0%, there is a problem that the Si content in the weld metal increases sharply and precipitates in the Laves Phase, resulting in deterioration of crack resistance.
Therefore, the content of SiO2 is preferably limited to 0.3 to 3.0%.
At least one of potassium (K), sodium (Na) and lithium (Li): 0.05 to 1.5%
The alkali metal lowers the ionization potential of the arc during welding to facilitate the generation of arc and can maintain a stable arc during welding. The effect of the alkali metal should be added by 0.05% or more. However, if the content exceeds 1.5%, welding fumes may occur excessively due to high vapor pressure. Here, the alkali metal includes at least one of potassium (K), sodium (Na) and lithium (Li) alkali metals, and the effect of addition of alkali metal in the present invention is independent of the respective content ratios.
F and Ca: 0.05 to 1.0%
The welding wire of the present invention has the effect of deepening the penetration and strengthening and stabilizing the arc when the fluorine (F) and potassium (Ca) are additionally added in the alkali metal and alkaline earth metal fluorine compounds. , The fluorine is generated in the arc in the arc of high temperature and reacts with hydrogen during welding to cause the dehydrogenation reaction, thereby effectively reducing the diffusible hydrogen. However, when it exceeds 1.0%, the welding fume Fume) is generated excessively, and TiO2 excessively reduces the slag viscosity of the molten pool in the rutile system, which is the main slag component, to form unstable beads. Therefore, the content thereof is preferably limited to 0.05 to 1.0%. Na2ZrF6, K2SiF6, Na2SiF6, Na3AlF6, Bb2SiF6, K2TiF6, K2ZrF6, LiF, LiBaF3, NaF and the like can be used
Al and Mg: 0.1 to 1.5%
Al and Mg are added as a reducing agent, which is a core component of the slag to ensure deoxidation of the wire and improve the welding performance. In order to secure the above-mentioned effect, it is preferable that at least one of Al and Mg is contained in an amount of 0.1% or more. If the amount exceeds 1.5%, the oxygen content in the melting paper is lowered due to excessive deoxidization during the welding process, The impurities can not be removed by the slag formation and the welding can be further disadvantageous.
The deoxidizer is added in the form of Al, Fe-Al, Al-Mg, Al-Zr, Mg, Ni-Mg, Mg-Al alloy or intermetallic compound.
The remainder of the present invention is nickel (Ni).
Nickel (Ni) is an austenite stabilizing element and has an effect of increasing the tensile strength by binding with Nb to form Ni3Nb precipitates.
More preferably, the Ni content can be limited to 58 to 70%.
In order to sufficiently obtain the above-mentioned effect, it is necessary to contain Ni at 58% or more. However, if the content exceeds 70%, the tensile strength may decrease.
In addition to the above-mentioned components, impurities that are not intended from the raw material or the surrounding environment may be inevitably incorporated in a conventional manufacturing process, and therefore, this can not be excluded. These impurities are not specifically mentioned in this specification, as they are known to any person skilled in the art of manufacturing.
The outer shell of the welding material is composed of 0.01 to 0.1% of C, 0.1 to 1.0% of Si, 0.01 to 1.0% of Mn, 18.0 to 25.0% of Cr, 0.01 to 1.0% of Ti, Impurity: 1.0% or less, and the remaining Ni.
The shell is a Ni-based alloy and functions to increase the content of Ni in the weld zone during welding. The reason for limiting the content of Ni and other impurities is as follows: high strength at high temperature, excellent oxidation resistance, To secure toughness at extremely low temperatures and to reduce defects such as cracks during welding.
Unlike the core, unlike the core, Mo and Nb are not contained. Thus, the tensile strength due to these components is similar to that of the stainless steel shell, the work hardening is low, and the electrical resistance is low.
The reason for limiting the content of the remaining components as described above is to satisfy the entire wire alloy composition.
As described above, according to the present invention, by controlling the alloy composition of the jacket relative to Inconel 625 and using the Ni-type jacket whose alloy content is controlled to the minimum, proper tensile strength and machining characteristics can be ensured and the Ni-based flux cored A wire welding material can be provided.
The diameter of the welding material is preferably about 0.9 to 1.6 mm, and the weight fraction of the sheath is preferably 50 to 90% in terms of the weight fraction of the entire welding material in consideration of the density of the sheath and the density of the core.
This type of sheath may be represented by a single sheath structure that surrounds the core of the alloy component.
All-position welding is possible by using a Ni-based flux cored wire that satisfies the alloy composition of the welding material and the alloy composition of the sheath surrounding the core, and has excellent tensile strength at the high temperature of the welded joint .
Hereinafter, the present invention will be described in detail with reference to Examples. However, the following examples are only for illustrating the present invention in more detail and do not limit the scope of the present invention.
( Example )
A welding material having components as shown in Table 1 and made up of the remaining Ni and other unavoidable impurities was prepared. However, the unit of each component is% by weight.
The composition of the jacket of the inventive material and the comparative material and the composition of the jacket are the same and the content of the entire welding material is different. The outer shell of the welding material is composed of 0.01 to 0.1% of C, 0.1 to 0.5% of Si, 0.1 to 0.5% of Mn, 19 to 25% of Cr, 0.1 to 1.0% of Ti, 0.1 to 1.0% of Ti, 1.0% or less, and the balance Ni.
Flux Cored Arc Welding (FCAW) was performed on each welding material.
In case of FCAW, welding was performed at 1.7 kJ / mm heat input rate under 100% CO2 condition and Ar + 15 ~ 25% CO2 condition. The diameter of the FCAW wire was 1.2 mm.
Then, the weldability, the cracks of the welded joints and the porosity are shown together in Table 1 below. Also, the components connected by '+' mean the content of one or more of the components.
In the present embodiment, the arc weldability was evaluated by comparing the arc stability and the slag peelability visually, and classified into three stages of A (excellent), B (poor) and C (poor).
The cracks and porosity were compared with each other by naked eyes, and the results were classified into three stages of A (excellent), B (poor) and C (poor).
In addition, the tensile strength of the welded joint using the following inventive and comparative examples satisfied at least 690 MPa, -196 DEG C impact toughness of 27 J or more.
From the results of Table 1, Examples 1 to 8 satisfying the alloy composition of the present invention were excellent in crack resistance and weldability.
In the case of Comparative Example 1 in which the content of TiO 2 was more than 15%, the slag content was excessive, so that the separation of the welded portion and the slag was not smooth and the weldability of the welded portion was insufficient.
In the case of Comparative Example 2, the content of TiO2 was less than 3.5%, the slag content was too small, and the slag inclusiveness was poor and it was difficult to secure a good weld bead.
In the case of Comparative Example 3, since the K + Na + Li content exceeded 1.5%, excessive welding fumes were generated due to high vapor pressure, and the slag flowability was excessively excessive, so that the slag shape in the vertical posture deteriorated and the beads flowed down.
In the case of Comparative Example 4, since the K + Na + Li content was less than 0.05%, the effect of reducing the ionization potential of the arc was insufficient, so that arc generation was not easy and it was difficult to secure a stable arc during welding.
In the case of Comparative Example 5, fume was generated excessively due to a high vapor pressure characteristic with an F + Ca fluoride content exceeding 1.0%, and TiO 2 excessively decreased the slag viscosity of the molten pool in the rutile system as a main slag component To form an unstable bead.
In the case of Comparative Example 6, the F + Ca fluoride content was less than 0.05%, and the effect of arc strengthening and stabilization was deteriorated, so that the penetration of the base material was not sufficiently deep.
In the case of Comparative Example 7, the SiO 2 content exceeded 3.0%, and the Si content of the welded portion was increased due to the reducing action, thereby promoting the generation of the Laves Phase. As a result, cracking occurred in the welded portion.
In the case of Comparative Example 8, the SiO 2 content was less than 0.3%, and the viscosity of the slag was so high that the flowability was lowered, so that the slag inclination during welding was not constant and the weld bead was not constant.
In the case of Comparative Example 9, the content of Al + Mg exceeds 1.5%, the oxygen content in the melting paper is lowered due to excessive deoxidation during the welding process, and the slag releasability is lowered due to the formation of oxidized slag.
In the case of Comparative Example 10, the Al + Mg content was less than 0.1% and the deoxidation effect of the weld portion was insufficient, thereby increasing the occurrence of pores and surface defects in the welded portion.
While the present invention has been particularly shown and described with reference to exemplary embodiments thereof, it is to be understood that the invention is not limited to the disclosed exemplary embodiments, but, on the contrary, It will be obvious to those of ordinary skill in the art.
Claims (4)
The welding material according to claim 1, wherein the welding material comprises 0.01 to 0.1% of C, 0.1 to 1.0% of Si, 0.01 to 1.0% of Mn, less than 0.035% of P and S, 18.0 to 25.0% of Cr, At least one of K, Na, and Li, and at least one of K, Na, and Li, and at least one of K, Na, and Li is contained in an amount of 7.0 to 11.0%, Ti of 0.01 to 1.0%, Nb of 3.0 to 4.5%, Fe of 0.01 to 5%, TiO2 of 3.5 to 15% : 0.05 to 1.5%, at least one of F and Ca: 0.05 to 1.0%, at least one of Al and Mg: 0.1 to 1.5%, remaining Ni and other unavoidable impurities,
Wherein the shell is composed of 0.01 to 0.1% of C, 0.1 to 1.0% of Si, 0.01 to 1.0% of Mn, 18.0 to 25.0% of Cr, 0.01 to 1.0% of Ti, 0.01 to 1.0% of Ti, : 1.0% or less, and the balance Ni.
Wherein the diameter of the welding material is 0.9 to 1.6 mm.
Wherein the shell is 50 to 90% in weight fraction of the weld material.
A Ni-based flux cored wire welding material having a tensile strength of 690 MPa or more, -196 DEG C, and an impact toughness of 27 J or more.
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| KR1020150116000A KR101760828B1 (en) | 2015-08-18 | 2015-08-18 | Ni-BASE FLUX CORED WIRE WELDING CONSUMABLE |
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| KR1020150116000A KR101760828B1 (en) | 2015-08-18 | 2015-08-18 | Ni-BASE FLUX CORED WIRE WELDING CONSUMABLE |
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Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR20190087846A (en) * | 2018-01-17 | 2019-07-25 | 현대종합금속 주식회사 | Ni base flux cored wire for cryogenic Ni alloy steel |
| KR102197134B1 (en) | 2019-11-29 | 2020-12-31 | 주식회사 세아에삽 | Ni based alloy flux cored wire |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2009018316A (en) | 2007-07-10 | 2009-01-29 | Nippon Steel Corp | Flux-cored welding wire for gas shielded arc welding of fire-resistant steel |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2009018316A (en) | 2007-07-10 | 2009-01-29 | Nippon Steel Corp | Flux-cored welding wire for gas shielded arc welding of fire-resistant steel |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| KR20190087846A (en) * | 2018-01-17 | 2019-07-25 | 현대종합금속 주식회사 | Ni base flux cored wire for cryogenic Ni alloy steel |
| KR102022448B1 (en) | 2018-01-17 | 2019-11-04 | 현대종합금속 주식회사 | Ni base flux cored wire for cryogenic Ni alloy steel |
| KR102197134B1 (en) | 2019-11-29 | 2020-12-31 | 주식회사 세아에삽 | Ni based alloy flux cored wire |
| WO2021107580A1 (en) | 2019-11-29 | 2021-06-03 | 주식회사 세아에삽 | Ni-based alloy flux-cored wire |
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| KR20170021521A (en) | 2017-02-28 |
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