Patent Application
20110171485
The present invention relates to flux-cored nickel-based alloy wires used in gas-shielded arc welding typically of nuclear reactors and pressure vessels. Specifically, the present invention relates to flux-cored nickel-based alloy wires which are adopted to gas-shielded arc welding typically of nickel-based alloys, incoloy alloys containing 30 to 40 percent by mass of Ni, steels for low temperature service containing 10 percent by mass or less of nickel (Ni), and super stainless steels. The flux-cored nickel-based alloy wires excel in weldability such as slag removability while suppressing spatter generation and give weld metals (weld beads) showing good pitting resistance and bead appearance and having satisfactory resistance to hot cracking.
Gas-shielded arc welding using flux-cored wires excels in working efficiency as compared to shielded metal arc welding and tungsten-inert-gas (TIG) welding, and its adaptation range grows year by year. Accordingly, strong demands have been made to develop and improve flux-cored wires adopted also to gas-shielded arc welding typically of nickel-based alloys, incoloy alloys containing 30 to 40 percent by mass of Ni, 9% nickel steels and other steels for low temperature service, and super stainless steels. Such widely-applicable flux-cored wires should be designed while giving consideration to weldability and weld metal properties such as resistance to cracking in sufficient consideration to the uses of the flux-cored wires.
Various investigations have been made in gas-shielded arc welding using flux-cored wires, to improve weldability and resistance to hot cracking. Typically, JP-A No. H06 (1994) -198488 discloses that a flux having specific contents of TiO2, SiO2 and ZrO2 as slag-forming materials allows the resulting weld bead to have better mechanical properties such as ductility, toughness, and resistance to hot cracking and to show better weldability.
JP-A No. 2000-343277 discloses that a flux-cored nickel-based alloy wire further containing an iron oxide and a manganese oxide can give a weld metal containing a less amount of Si and showing better resistance to hot cracking.
The techniques disclosed in the two patent literatures are intended to improve the resistance to hot cracking but disadvantageously cause welding defects, such as pits, of the weld beads. The present inventors have proposed in JP-A No. 2008-246507 a technique for improving pitting resistance by specifying the contents of TiO2, SiO2 and ZrO2 as slag-forming materials, the total content of these slag-forming materials, and the MnO2 content. This technique is intended to prevent welding defects such as pits which are generated when the techniques disclosed in these patent literatures are adopted.
The above-mentioned known techniques, however, have the following disadvantages. The flux-cored nickel-based alloy wire disclosed in JP-A No. H06(1994) -198488 often suffers from welding defects, such as pits, on surfaces of beads in horizontal fillet welding and horizontal welding, in which a molten metal solidifies at a higher rate than that in flat welding. In addition, the wire may suffer from degraded arc stability during welding operation, or may suffer from degraded weldability in vertical upward welding in which the molten metal solidifies at a lower rate.
JP-A No. 2000-343277 discloses the technique for improving the resistance to hot cracking by adding iron oxides and manganese oxides and thereby reducing the Si content in the weld metal, as described above. In some compositions, however, this technique may fail to control the Si content in the weld metal and may cause degraded resistance to hot cracking, because the iron oxides and manganese oxides are added to a flux in which the contents of TiO2, SiO2, ZrO2, Al2O3, CaO, Na2O and K2O are specified only with respect to the total amount of them.
As is described above, the present inventors have proposed in JP-A No. 2008-246507 a technique for improving resistance to pits which are generated when the known techniques are adopted, by specifying the respective contents and total content of TiO2, SiO2 and ZrO2 as slag-forming materials as well as specifying the MnO2 content. Even this technique, however, may suffer from degraded arc stability during welding or may suffer from poor resistance to hot cracking in some compositions.
The present invention has been made under these circumstances, and an object of the present invention is to provide a flux-cored nickel-based alloy wire which excels in weldability in welding of all positions performed typically on 9% nickel steels and nickel-based alloy steels and which can give a weld metal showing good pitting resistance and bead appearance and having satisfactory resistance to hot cracking.
Specifically, the present invention provides, in an embodiment, a flux-cored nickel-based alloy wire which includes a sheath composed of a nickel-based alloy; and a flux filled in the sheath, in which the sheath contains nickel (Ni) in a content of 50.0 percent by mass or more, the flux contains, based on the total mass of the wire, TiO2 in a content of 3 to 11 percent by mass; SiO2 in a content of 0.2 to 1.3 percent by mass; ZrO2 in a content of 1 to 3 percent by mass; one or more manganese oxides in a content in terms of MnO2 of 0.3 to 1.0 percent by mass; and one or more compounds selected from the group consisting of sodium (Na) compounds, potassium (K) compounds, and (Li) lithium compounds in a total content in terms of Na, K, and Li, respectively, of 0.2 to 1.0 percent by mass, and the flux has a ratio of the total of the TiO2 and ZrO2 contents to the SiO2content (([TiO2]+[ZrO2])/[SiO2]) of 5.0 to 14.5, where [TiO2], [SiO2] and [ZrO2] represent the TiO2, SiO2 and ZrO2 contents, respectively.
In the flux-cored nickel-based alloy wire according to the present invention, it is preferred that the sheath has controlled contents of carbon (C), silicon (Si), manganese (Mn), phosphorus (P), sulfur (S), copper (Cu), vanadium (V) and cobalt (Co) so as to have, based on the total mass of the sheath, a C content of 0.02 percent by mass or less, a Si content of 0.08 percent by mass or less, a Mn content of 1.0 percent by mass or less, a P content of 0.04 percent by mass or less, a S content of 0.03 percent by mass or less, a Cu content of 0.50 percent by mass or less, a V content of 0.35 percent by mass or less, and a Co content of 2.5 percent by mass or less, and the sheath contains, based on the total mass of the sheath, chromium (Cr) in a content of 14.5 to 16.5 percent by mass, molybdenum (Mo) in a content of 15.0 to 17.0 percent by mass, iron (Fe) in a content of 4.0 to 7.0 percent by mass, and tungsten (W) in a content of 3.0 to 4.5 percent by mass.
In the flux-cored nickel-based alloy wire according to the present invention, the sheath preferably occupies 70 to 80 percent by mass of the total mass of the wire.
In the flux-cored nickel-based alloy wire according to the present invention, the flux contains TiO2, SiO2, ZrO2, manganese oxides, and one or more of sodium compounds, potassium compounds and lithium compounds within appropriate ranges, and the flux has a ratio of the total of the TiO2 and ZrO2 contents to the SiO2 content within a specific appropriate range. This allows excellent weldability in welding of all positions and gives a weld metal showing good pitting resistance and bead appearance and having satisfactory resistance to hot cracking.
The present inventors made investigations on the composition of flux components and have developed the flux composition according to the present invention, so as to improve the resistance to hot cracking and the weldability. The present inventors proposed the technique disclosed in JP-A No. 2008-246507 in order to solve the problems of degraded arc stability and weldability in some welding positions. These problems occur when the flux-cored nickel-based alloy wires according to the known techniques are adopted. However, even the proposed technique may suffer from degraded arc stability during welding or may suffer from degraded resistance to hot cracking in some compositions. A weld metal composed of a nickel-based alloy solidifies as a single layer of austenite (γ) and is thereby inherently susceptible to solidification cracking. In particular, of chemical composition of weld metal, P, S, and Si components have low solid-liquid distribution coefficients in the nickel-based alloy, thereby form eutectic mixtures having low melting points (e.g., in the case of silicon compounds, they form Ni—Ni3Si and Ni—Nb—Si eutectic mixtures), and significantly cause the resulting nickel-based alloy weld metal to have higher susceptibility to solidification cracking. The present inventors made intensive experiments and investigations in order to solve the problems of the known flux-cored nickel-based alloy wires which suffer from degraded resistance to hot cracking, or suffer from degraded arc stability in some compositions of the flux-cored wires, or suffer from poor weldability in some welding positions. As a result, the present inventors have found that a weld metal of a nickel-based alloy can be suppressed from containing remained silicon and can thereby be prevented from degradation in resistance to hot cracking, by specifying the SiO2 content of the flux, appropriately specifying the ratio between the SiO2 content as a slag-forming material and the total amount of TiO2 and ZrO2 as other slag-forming materials, and appropriately adding one or more manganese oxides within an appropriate range. The present inventors have further found that, in addition to the above conditions, the addition of an appropriate amount of sodium compounds, potassium compounds, and lithium compounds prevents degradation in arc stability during welding and degradation in weldability in some welding positions.
The flux-cored nickel-based alloy wire according to the present invention preferably has a composition of the sheath and a ratio of the sheath occupying in the entire wire within the following ranges. Specifically, the composition of the sheath is preferably specified as follows, as a precondition for the weld metal to have a component composition that meets the composition prescribed in American Welding Society (AWS) Standards Class A5.34 ENiCrMo4Tx-y. The sheath preferably has controlled contents of C, Si, Mn, P, S, Cu, V and Co so as to have, based on the total mass of the sheath, a C content of 0.02 percent by mass or less, a Si content of 0.08 percent by mass or less, a Mn content of 1.0 percent by mass or less, a P content of 0.04 percent by mass or less, a S content of 0.03 percent by mass or less, a Cu content of 0.50 percent by mass or less, a V content of 0.35 percent by mass or less, and a Co content of 2.5 percent by mass or less, and the sheath preferably contains, based on the total mass of the sheath, Cr in a content of 14.5 to 16.5 percent by mass, Mo in a content of 15.0 to 17.0 percent by mass, Fe in a content of 4.0 to 7.0 percent by mass, and W in a content of 3.0 to 4.5 percent by mass. This composition falls within the range of components prescribed in AWS A5.14 ERNiCrMo4. Thus, by using a sheath having such composition falling within the range of components prescribed in AWS A5.14 ERNiCrMo4 to give a weld metal having a composition that meets the requirements in AWS A5.34 ENiCrMo4Tx-y, the resulting weld metal exhibits excellent resistance to hot cracking and superior pitting resistance. The flux-cored nickel-based alloy wire according to the present invention preferably has a sheath ratio (a ratio of the sheath mass to the total mass of the flux-cored wire) of 70 to 80 percent by mass. In a flux-cored wire having such a high sheath ratio, the composition of the sheath affects the composition of the weld metal.
The flux-cored nickel-based alloy wire according to the present invention is advantageously used typically for butt welding using, as base metals, nickel-based alloys, incoloy alloys containing 30 to 40 percent by mass of Ni, 9% nickel steels and other steels for low temperature service, and super stainless steels; and build-up welding using, as base metals, clad steels, low-alloy steels, low-alloy heat-resistant steels, and stainless steels.
Reasons for specifying numerical values relating to the flux-cored nickel-based alloy wire will be described below.
“TiO2 content in the flux [TiO2]: 3 to 11 percent by mass based on the total mass of the wire”
Titanium dioxide (TiO2) forms a uniform slag covering and improves the arc stability. Therefore, TiO2 is thereby added as a main component of slag-forming materials. Exemplary TiO2 sources usable herein include rutile, leucoxene, potassium titanate, sodium titanate, and calcium titanate. TiO2, if its content in the flux is less than 3 percent by mass based on the total mass of the wire, may not sufficiently exhibit the activities as the slag-forming material. In contrast, TiO2, if its content in the flux is more than 11 percent by mass based on the total mass of the wire, is present as a slag-forming material in an excessive amount in the wire and thereby causes excessive generation of the slag during welding. This causes the slag to drip from the weld bead to often cause slag inclusion of the weld bead and to cause degraded pitting resistance. Accordingly, the TiO2 content in the flux is herein specified to be 3 to 11 percent by mass based on the total mass of the wire. A more preferred lower limit of the TiO2 content is 5 percent by mass, and a more preferred upper limit thereof is 8 percent by mass.
“SiO2 content in the flux [SiO2]: 0.2 to 1.3 percent by mass based on the total mass of the wire”
Silicon dioxide (SiO2) is added as a slag-forming material to increase the viscosity of the slag and to give a good bead shape. Exemplary raw materials for SiO2 usable herein include silica sand, potassium feldspar, wollastonite, sodium silicate, and potassium silicate. SiO2, if its content in the flux is less than 0.2 percent by mass based on the total mass of the wire, may not sufficiently exhibit the activities as the slag-forming material. In contrast, SiO2, if its content in the flux is more than 1.3 percent by mass based on the total mass of the wire, may cause degraded slag removability. Additionally, SiO2, if added in an excessive amount, may cause the weld bead to have an excessively high Si content to thereby often have degraded resistance to hot cracking, because SiO2 is susceptible to reduction by a strongly deoxidizing element such as Ti. Accordingly, the SiO2 content in the flux is specified to be 0.2 to 1.3 percent by mass based on the total mass of the wire. A more preferred lower limit of the SiO2 content is 0.6 percent by mass, and a more preferred upper limit thereof is 1.2 percent by mass.
“ZrO2 content in the flux [ZrO2]: 1 to 3 percent by mass based on the total mass of the wire”
Zirconium dioxide (ZrO2) helps the arc to be blown more satisfactorily and to be more stable even at low welding currents. This component also accelerates the solidification of the slag and thereby improves the weldability in vertical upward welding. Exemplary ZrO2 sources usable herein include zircon sand and zirconia ZrO2, if its content in the flux is less than 1 percent by mass based on the total mass of the wire, may not sufficiently effectively improve the arc stability and weldability. In contrast, ZrO2, if its content in the flux is more than 3 percent by mass based on the total mass of the wire, may cause the slag to start to solidify at a higher temperature and to solidify more slowly, and this may prevent a gas, which is generated from the weld metal during solidification, from escaping via the slag during solidification and may thereby increase the number of pits generated in the weld bead. Accordingly, the ZrO2 content herein is specified to be 1 to 3 percent by mass based on the total mass of the wire.
“Manganese oxide content (in terms of MnO2) in the flux: 0.3 to 1.0 percent by mass based on the total mass of the wire”
At temperatures in the range of 0° C. to 2400° C., silicon oxides have a standard free energy of formation lower than that of manganese oxides and can react more stably than manganese oxides do. Specifically, the addition of MnO2 to the flux accelerates the reactions of MnO2→Mn+O2 and Si+O2→SiO2 in the molten metal, and SiO2 after the reaction rises to the surface as a slag. Accordingly, MnO2 impedes SiO2 from being reduced into Si and from remaining as elementary Si in the weld metal. In addition, MnO2 has a low melting point of 550° C., and the addition of MnO2 to the flux allows the molten slag to start to solidify at a lower temperature, and this prevents the gas, which is generated from the weld metal during solidification, from remaining in the weld bead and thereby prevents the pit generation. Manganese oxides, if its content in the flux is less than 0.3 percent by mass based on the total mass of the wire, may not sufficiently exhibit the effects of preventing Si remaining in the weld metal and of preventing pit generation and may cause degraded resistance to hot cracking. In contrast, manganese oxides, if its content in the flux is more than 1.0 percent by mass based on the total mass of the wire, may cause the slag to easily penetrate (fuse with) the bead surface to thereby impair slag removability and may cause the molten slag to solidify at a lower temperature, thus impairing the workability in vertical upward welding. Accordingly, the manganese oxide content in the flux is specified herein to be 0.3 to 1.0 percent by mass based on the total mass of the wire. A more preferred lower limit of the manganese oxide content is 0.4 percent by mass, and a more preferred upper limit thereof is 0.9 percent by mass.
It should be noted that the term “manganese oxides” means and includes oxidized manganese (also including other manganese oxides than MnO2) but does not include elementary manganese (manganese alloys). The amounts of the other manganese oxides than MnO2 are converted into the mass of MnO2 containing the same amount of manganese and added to the “manganese oxide content”.
“Sodium compounds, potassium compounds, and lithium compounds in the flux: in a total content of these compounds in terms of Na, K and Li of 0.2 to 1.0 percent by mass based on the total mass of the wire”
Sodium (Na), potassium (K), and lithium (Li) in the flux act as arc stabilizers and suppress spatter generation. In the present invention, Na, K, and Li are added as sodium compounds, potassium compounds, and lithium compounds, respectively. Specific examples of such compounds usable herein include LiF, NaF, KF, Na3AlF6, K2SiF6, K2TiF6, albite, and potash feldspar. Sodium compounds, potassium compounds, and lithium compounds, if in a total content in the flux in terms of Na, K, and Li, respectively, of less than 0.2 percent by mass based on the total mass of the wire, may not sufficiently exhibit their activities as arc stabilizers and may cause degraded pitting resistance. In contrast, sodium compounds, potassium compounds, and lithium compounds, if contained in the flux in a total content of more than 1.0 percent by mass, may cause increased spatter generation contrarily. Accordingly, the total content of sodium compounds, potassium compounds, and lithium compounds in the flux in terms of Na, K and Li is specified to be 0.2 to 1.0 percent by mass based on the total mass of the wire. A more preferred upper limit of the total content of these compounds is 0.7 percent by mass.
“Ratio of the total of the TiO2 and ZrO2 contents to the SiO2 content in the flux (([TiO2]+[ZrO2])/[SiO2]): 5.0 to 14.5”
SiO2 allows the slag to have a higher viscosity and allows the weld bead to show a better shape, as described above. However, if the ratio of the total of the TiO2 and ZrO2 contents to the SiO2 content is more than 14.5, the slag may have degraded flowability and may be formed unevenly, and this may often cause slag inclusion and degraded wettability of the bead. Additionally, such a high ratio may cause the slag to start to solidify at a higher temperature and to solidify more slowly, and this may impede the discharge out of a gas, which has been generated from the weld metal during solidification, via the slag during solidification and thereby increase the number of pits generated in the weld bead. In contrast, if the ratio of the total of the TiO2 and ZrO2 contents to the SiO2 content is less than 5.0, the slag is liable to attach (fuse with) the bead and shows inferior slag removability. Accordingly, the ratio of the total of the TiO2 and ZrO2 contents to the SiO2 content (([TiO2]+[ZrO2])/[SiO2]) herein is specified to be 5.0 to 14.5. The ratio of the total of the TiO2 and ZrO2 contents to the SiO2 content is more preferably 7.0 to 14.0.
The flux-cored nickel-based alloy wire according to the present invention may further contain, in addition to the above-mentioned components, carbonates, CaF2 and other basic materials. The addition of carbonates, CaF2 and other basic materials, however, may often cause degraded arc stability and increased spatter generation, thus often causing degraded weldability. Accordingly, these carbonates, CaF2 and other basic materials can be added in an amount of 0.1 percent by mass or less based on the total mass of the wire.
The present invention will be illustrated in further detail with reference to several working examples demonstrating advantageous effects of the flux-cored nickel-based alloy wire according to the embodiment of the present invention in comparison with comparative examples thereof. Initially, a series of cylindrical sheathes 11a (Types A to C) as illustrated in
0.12
0.021
21.8
3.2
0
1.4
0.1
95.0
0.5
3.2
2.0
12.0
0.2
1.5
16.7
0
0
0.1
1.1
Horizontal fillet welding was performed using each of the flux-cored wires 11 of Nos. 1 to 29 manufactured according to the above method. The arc stability and spatter suppression during the welding, and pitting resistance, bead appearance and slag removability of the weld bead were evaluated.
The horizontal fillet welding was performed using a SM490A steel sheet having a thickness of 12 mm, a width of 80 mm, and a length of 300 mm as a base metal. The welding was performed under conditions of a welding current of 200 A (direct current, wire positive), an arc voltage of 28 V, and a welding speed of 30 cm per minute, using a mixture of argon and 20% CO2 as a shielding gas supplied at a flow rate of 25 liters per minute.
The welding operations using the flux-cored wires gave weld metals having compositions corresponding to the compositions of the total components of the weld metal shown in following Table 4. These compositions are in accordance with the compositions of sheath Types A to C in Table 1 and with the compositions of the wires Nos. 1 to 29 in Tables 2-1, 2-2, and 2-3. The total components of the weld metals were analyzed by sampling the weld bead as illustrated in
The arc stability and spatter suppression during welding, and the pitting resistance, bead appearance and slag removability of the weld beads respectively obtained from flux-cored wires according to the examples and comparative examples were evaluated, and the results are shown in Table 5 below. The arc stability and spatter suppression during welding, and the bead appearance and slag removability of the weld beads were respectively evaluated as “AA” when they were very good; evaluated as “BB” when they were good; evaluated as “CC” when they were somewhat poor; and evaluated as “DD” when they were poor. The pitting resistance was evaluated by the number of dyed spots detected through a dye penetrant inspection on the bead surface. In this inspection, end portions 50 mm from the toe and heel of the weld bead were excluded from portions to be evaluated. A sample having an average number of generated pits per 50 mm of the length of the bead of 0 was evaluated as “AA”; one having an average number of 1 to 10 was evaluated as “BB”; one having an average number of 11 to 30 was evaluated as “CC”; and one having an average number of 31 or more was evaluated as “DD”.
Independently, restraint cracking tests were performed on the weld beads obtained according to the examples and comparative examples, to evaluate the resistance to hot cracking. In the restraint cracking tests, two SM490A steel sheets each having a thickness of 20 mm and being illustrated in Table 3 were used as base metals, and single bead welding was performed on the base metals with an automatic welder. The base metals had a width of 125 mm and a length of 300 mm, were arranged as facing in a distance of 2 mm, and had a slope down to one half of the thickness so as to have an included angle of 60°, as illustrated in
Separately, vertical upward welding of a fillet T joint was performed semi-automatically using two SM490A steel sheets each having a thickness of 12 mm, a width of 80 mm, and a length of 300 mm as base metals, and the weldability in this welding was evaluated. The welding was performed at a welding current of 150 A (direct current, wire positive) and an arc voltage of 26 V while supplying a mixture of argon and 20% CO2 as the shielding gas at a flow rate of 25 liters per minute. The welding speed was set to 6 cm per minute. A sample showing very good weldability (no bead drooling (bead dripping) even at a welding current of 160 to 170 A) was evaluated as “AA”, one showing good weldability was evaluated as “BB”, one showing bead drooling was evaluated as “CC”, and one failing to undergo welding was evaluated as “DD”. As a comprehensive evaluation, a sample evaluated as “AA” in all the pitting resistance, arc stability, bead appearance and slag removability, weldability in vertical upward welding, spatter suppression, and resistance to hot cracking was evaluated as “AA” in comprehensive evaluation; one evaluated as “BB” in at least one of the above properties but evaluated as “AA” in the other properties was evaluated as “BB” in comprehensive evaluation; one evaluated as “DD” in at least one property was evaluated as “DD” in comprehensive evaluation; and one evaluated as “CC” in at least one properties but evaluated not as “DD” in the other properties was evaluated as “CC” in comprehensive evaluation. The comprehensive evaluations of the samples according to the examples and comparative examples are also shown in Table 5.
0.31
0.29
0.30
0.38
Table 5 demonstrates that Examples Nos. 1 to 15 satisfying the conditions as in the present invention showed excellent arc stability and spatter suppression during welding, showed satisfactory weldability in vertical upward welding, had good pitting resistance, bead appearance and slag removability of the weld bead, and showed satisfactory resistance to hot cracking. Comparative Example No. 16 had a SiO2 content in the flux higher than the range specified in the present invention, thereby showed degraded bead appearance and slag removability, and had poor resistance to hot cracking. Comparative Example No. 17 had a SiO2 content in the flux lower than the range specified in the present invention and showed degraded bead appearance and slag removability. This sample also had a ratio of the total of the TiO2 and ZrO2 contents to the SiO2 content higher than the range specified in the present invention and thereby showed an increased number of pits generated in the weld bead.
Comparative Example No. 18 had a ZrO2 content in the flux lower than the range specified in the present invention and thereby did not show sufficiently effectively improved weldability even though ZrO2 was added. Comparative Example No. 19 had a ZrO2 content in the flux and a ratio of the total of the TiO2 and ZrO2 contents to the SiO2 content both higher than the ranges specified in the present invention and thereby showed degraded pitting resistance. Comparative Example No. 20 had a TiO2 content in the flux lower than the range specified in the present invention, thereby showed degraded arc stability to cause poor weldability, and had degraded bead appearance and slag removability. Comparative Example No. 21 had a TiO2 content in the flux higher than the range specified in the present invention and thereby showed degraded pitting resistance.
Comparative Example No. 22 had a manganese oxide content in the flux lower than the range specified in the present invention, thereby showed degraded pitting resistance, failed to prevent silicon from remaining in the weld metal, and showed degraded resistance to hot cracking. Comparative Example No. 23 had a manganese oxide content in the flux higher than the range specified in the present invention, thereby showed degraded slag removability, and showed degraded weldability in vertical upward welding due to a lowered minimum temperature of solidification of the molten slag. Comparative Example No. 24 had a ratio of the total of the TiO2 and ZrO2 contents to the SiO2 content in the flux lower than the range specified in the present invention, and thereby showed degraded slag removability and weldability in vertical upward welding. Comparative Example No. 25 had a ratio of the total of the TiO2 and ZrO2 contents to the SiO2 content in the flux higher than the range specified in the present invention, and thereby showed degraded pitting resistance.
Comparative Example No. 26 had a total content of sodium compounds, potassium compounds, and lithium compounds in the flux in terms of Na, K and Li, respectively, lower than the range specified in the present invention, thereby showed degraded arc stability to cause insufficient spatter suppression, and had degraded pitting resistance. Comparative Example No. 27 had a total contents of sodium compounds, potassium compounds, and lithium compounds in the flux in terms of Na, K and Li, respectively, higher than the range specified in the present invention and thereby showed an increased spatter generation. Comparative Examples No. 28 and No. 29 did not contain manganese oxide and thereby showed degraded pitting resistance and inferior resistance to hot cracking.
Of Examples Nos. 1 to 15 satisfying the conditions in the present invention, Examples Nos. 1 to 5 are examples having compositions of the sheath within the preferred range specified in the present invention and thereby showed resistance to hot cracking superior to that of Examples Nos. 6 to 15 having compositions of the sheath not falling within the preferred range.
| Number | Date | Country | Kind |
|---|---|---|---|
| 2010-003440 | Jan 2010 | JP | national |
