US3914506A - Welding material for austenitic stainless steels - Google Patents
Welding material for austenitic stainless steels Download PDFInfo
- Publication number
- US3914506A US3914506A US374966A US37496673A US3914506A US 3914506 A US3914506 A US 3914506A US 374966 A US374966 A US 374966A US 37496673 A US37496673 A US 37496673A US 3914506 A US3914506 A US 3914506A
- Authority
- US
- United States
- Prior art keywords
- welding
- deposited metal
- metal
- ferrite
- tantalum
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Expired - Lifetime
Links
- 238000003466 welding Methods 0.000 title claims abstract description 79
- 239000000463 material Substances 0.000 title claims abstract description 21
- 229910001220 stainless steel Inorganic materials 0.000 title claims description 11
- 229910052751 metal Inorganic materials 0.000 claims abstract description 99
- 239000002184 metal Substances 0.000 claims abstract description 99
- 229910052715 tantalum Inorganic materials 0.000 claims abstract description 32
- 239000000203 mixture Substances 0.000 claims abstract description 26
- 229910000859 α-Fe Inorganic materials 0.000 claims abstract description 23
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 16
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 14
- 239000000126 substance Substances 0.000 claims abstract description 13
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 9
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 9
- 229910052717 sulfur Inorganic materials 0.000 claims abstract description 9
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 8
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 7
- 238000000576 coating method Methods 0.000 claims description 14
- 239000011248 coating agent Substances 0.000 claims description 12
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 7
- 229910000963 austenitic stainless steel Inorganic materials 0.000 claims description 6
- 230000006872 improvement Effects 0.000 claims description 5
- 239000012535 impurity Substances 0.000 claims description 5
- 229910052742 iron Inorganic materials 0.000 claims description 3
- 239000000945 filler Substances 0.000 abstract description 32
- 230000004907 flux Effects 0.000 abstract description 12
- 229910052750 molybdenum Inorganic materials 0.000 abstract description 4
- 229910052802 copper Inorganic materials 0.000 abstract description 2
- GUVRBAGPIYLISA-UHFFFAOYSA-N tantalum atom Chemical compound [Ta] GUVRBAGPIYLISA-UHFFFAOYSA-N 0.000 description 25
- 238000005260 corrosion Methods 0.000 description 21
- 230000007797 corrosion Effects 0.000 description 21
- 239000010955 niobium Substances 0.000 description 17
- 150000002739 metals Chemical class 0.000 description 16
- 238000012360 testing method Methods 0.000 description 13
- 238000005336 cracking Methods 0.000 description 11
- 239000011651 chromium Substances 0.000 description 10
- 239000011261 inert gas Substances 0.000 description 8
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 7
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 6
- 238000002844 melting Methods 0.000 description 6
- 230000008018 melting Effects 0.000 description 6
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 5
- 206010037660 Pyrexia Diseases 0.000 description 4
- 230000015572 biosynthetic process Effects 0.000 description 4
- 238000010438 heat treatment Methods 0.000 description 4
- 238000000034 method Methods 0.000 description 4
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 3
- 230000009286 beneficial effect Effects 0.000 description 3
- 239000008199 coating composition Substances 0.000 description 3
- NFFIWVVINABMKP-UHFFFAOYSA-N methylidynetantalum Chemical compound [Ta]#C NFFIWVVINABMKP-UHFFFAOYSA-N 0.000 description 3
- 229910052757 nitrogen Inorganic materials 0.000 description 3
- 229910052760 oxygen Inorganic materials 0.000 description 3
- 239000001301 oxygen Substances 0.000 description 3
- 230000035945 sensitivity Effects 0.000 description 3
- 229910003468 tantalcarbide Inorganic materials 0.000 description 3
- 229910017082 Fe-Si Inorganic materials 0.000 description 2
- 229910017133 Fe—Si Inorganic materials 0.000 description 2
- 239000004115 Sodium Silicate Substances 0.000 description 2
- 229910000831 Steel Inorganic materials 0.000 description 2
- 241000272534 Struthio camelus Species 0.000 description 2
- 238000004458 analytical method Methods 0.000 description 2
- 238000000137 annealing Methods 0.000 description 2
- 239000007864 aqueous solution Substances 0.000 description 2
- 230000008901 benefit Effects 0.000 description 2
- 239000010949 copper Substances 0.000 description 2
- 239000013078 crystal Substances 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000002474 experimental method Methods 0.000 description 2
- 238000005204 segregation Methods 0.000 description 2
- NTHWMYGWWRZVTN-UHFFFAOYSA-N sodium silicate Chemical compound [Na+].[Na+].[O-][Si]([O-])=O NTHWMYGWWRZVTN-UHFFFAOYSA-N 0.000 description 2
- 229910052911 sodium silicate Inorganic materials 0.000 description 2
- 238000007711 solidification Methods 0.000 description 2
- 230000008023 solidification Effects 0.000 description 2
- 239000010935 stainless steel Substances 0.000 description 2
- 239000010959 steel Substances 0.000 description 2
- 230000009466 transformation Effects 0.000 description 2
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 1
- 206010011376 Crepitations Diseases 0.000 description 1
- 229910000604 Ferrochrome Inorganic materials 0.000 description 1
- 229910000616 Ferromanganese Inorganic materials 0.000 description 1
- 229910000863 Ferronickel Inorganic materials 0.000 description 1
- 229910000519 Ferrosilicon Inorganic materials 0.000 description 1
- 208000037656 Respiratory Sounds Diseases 0.000 description 1
- 229910004517 TaFe Inorganic materials 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 238000004220 aggregation Methods 0.000 description 1
- 230000002776 aggregation Effects 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 229910001566 austenite Inorganic materials 0.000 description 1
- 239000010953 base metal Substances 0.000 description 1
- 239000011230 binding agent Substances 0.000 description 1
- 239000007795 chemical reaction product Substances 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- UFGZSIPAQKLCGR-UHFFFAOYSA-N chromium carbide Chemical compound [Cr]#C[Cr]C#[Cr] UFGZSIPAQKLCGR-UHFFFAOYSA-N 0.000 description 1
- -1 chromium carbide Chemical class 0.000 description 1
- 239000011247 coating layer Substances 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 230000008602 contraction Effects 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- BQJTUDIVKSVBDU-UHFFFAOYSA-L copper;sulfuric acid;sulfate Chemical compound [Cu+2].OS(O)(=O)=O.[O-]S([O-])(=O)=O BQJTUDIVKSVBDU-UHFFFAOYSA-L 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 238000001035 drying Methods 0.000 description 1
- 230000009931 harmful effect Effects 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
- 238000011835 investigation Methods 0.000 description 1
- DALUDRGQOYMVLD-UHFFFAOYSA-N iron manganese Chemical compound [Mn].[Fe] DALUDRGQOYMVLD-UHFFFAOYSA-N 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- 230000001473 noxious effect Effects 0.000 description 1
- BPUBBGLMJRNUCC-UHFFFAOYSA-N oxygen(2-);tantalum(5+) Chemical compound [O-2].[O-2].[O-2].[O-2].[O-2].[Ta+5].[Ta+5] BPUBBGLMJRNUCC-UHFFFAOYSA-N 0.000 description 1
- 230000036961 partial effect Effects 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 230000002829 reductive effect Effects 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 238000003303 reheating Methods 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 230000000717 retained effect Effects 0.000 description 1
- 239000002893 slag Substances 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 230000000087 stabilizing effect Effects 0.000 description 1
- QAOWNCQODCNURD-UHFFFAOYSA-N sulfuric acid Substances OS(O)(=O)=O QAOWNCQODCNURD-UHFFFAOYSA-N 0.000 description 1
- MZLGASXMSKOWSE-UHFFFAOYSA-N tantalum nitride Chemical compound [Ta]#N MZLGASXMSKOWSE-UHFFFAOYSA-N 0.000 description 1
- 229910001936 tantalum oxide Inorganic materials 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
- 229910003470 tongbaite Inorganic materials 0.000 description 1
- 238000012546 transfer Methods 0.000 description 1
Classifications
-
- 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
- B23K35/3053—Fe as the principal constituent
- B23K35/308—Fe as the principal constituent with Cr as next major constituent
- B23K35/3086—Fe as the principal constituent with Cr as next major constituent containing Ni or Mn
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
- Y10T428/00—Stock material or miscellaneous articles
- Y10T428/29—Coated or structually defined flake, particle, cell, strand, strand portion, rod, filament, macroscopic fiber or mass thereof
- Y10T428/2913—Rod, strand, filament or fiber
- Y10T428/2933—Coated or with bond, impregnation or core
- Y10T428/294—Coated or with bond, impregnation or core including metal or compound thereof [excluding glass, ceramic and asbestos]
- Y10T428/2951—Metal with weld modifying or stabilizing coating [e.g., flux, slag, producer, etc.]
Definitions
- ABSTRACT A welding material with a chemical composition so adjusted that it forms a deposited metal which will contain as component elements not more than 0.15% C, 15.0 30.0% Cr, 8.0 40.0% Ni, not more than 2.5% Mn, not more than 1.5% Si, not more than 3.0% Mo, not more than 4.0% Cu, not more than 0.045% P, not more than 0.030% S, and not more than 0.30% Nb, and will also contain not more than 5% ferrite, characterized in that a suitable amount of Ta is chosen so that the deposited metal will contain 0.40 3.0% Ta, and the mixture is added to at least either filler metal (including the core wire for shielded arc welding) or flux.
- This invention relates to a welding material for austenitic stainless steels. More particularly, the invention concerns a welding material which, when used in welding austenitic stainless steels, can produce deposited metal free from crack due to the heat of welding and improved in corrosion resistance and strength for use at high temperatures.
- Deposited metal with not more than 5% ferrite may be in service for long at elevated temperature or may be stress relieved by annealing without any sacrifice of its corrosion resistance, hightemperature strength and other desirable properties.
- the limitation of the ferrite content is thus essential for the improvement of various properties of the metal deposited by welding on austenitic stainless steels.
- the present invention resides in a welding material of a chemical composition so adjusted that the elementary contents of the deposited metal thereby formed are not more than 0.15% C, 15.0 30.0% Cr, 8.0 40.0% Ni, not more than 2.5% Mn, not more than 1.5% Si, not more than 3.0% Mo, not more than 4.0%
- Cu not more than 0.045% P, not more than 0.030% S, not more than 0.3% Nb, and not more than 5% ferrite, characterized in that Ta is added in such an amount that the resulting deposit may contain 0.4 3.0% Ta and that the material of this composition is added beforehand to at least either filler metal (including the core wire of a coated electrode) or flux.
- Tantalum which is added to at least either filler metal of flux in accordance with this invention, has such a close affinity for oxygen, nitrogen, and carbon, that it reacts with oxygen and nitrogen in the welding arc to give tantalum oxide and tantalum nitride. Because of their high melting points the reaction products (TaO, m.p. over 3000C, and TaN, m.p. 3100C) form crystal nuclei as the molten metal begins to solidify and make the deposited metal very fine in grain size. Consequently the deposit has microcrystalline grains and is completely protected against cracking which may otherwise result from welding.
- the low crack sensitivity of the deposited metal with refined grains may well be explained as follows.
- the welding crack of austenitic stainless steel is a hot crack that occurs at a temperature just short of the solidification point, and this is caused by the opening due to the contraction stress on solidification after welding of the low-melting-point impurities that have precipitated at the grain boundaries of the deposit.
- tantalum gives Ta compounds (TaO and TaN) having high melting points which in turn effect grain refining of the deposited metal and thereby increase the total volume of the grain boundaries and decrease the concentration of the low-melting-point foreign matter at the boundaries to such an extent that the possibility of welding crack is eliminated.
- tantalum has a stronger affinity for carbon than chromium and iron do. Therefore, the metal melted by the heat of welding arc is in a half melted and high-temperature state in its course of so lidification produces a tantalum carbide and fixes the carbon. This reduces the amount of free carbon to an extremely small amount and suppresses formation of noxious carbides, such as, chromium carbide, during cooling or reheating over 600C. Accordingly the corrosion resistance is retained and not affected in service. Moreover, the tantalum carbide with a high melting point (3827C) forms crystal nuclei in much the same way as the oxide and nitride to refine the grains of the deposited metal and prevent the welding crack.
- the high melting point (2996C) of Ta makes it impossible to form any foreign matter with a low melting point, and eliminates the danger of welding crack.
- the tantalum thus brought into the deposit strengthens the austenite structure and the solid solution, and therefore the deposited metal itself.
- a further benefit is that the fine precipitates of tantalum and the like exhibit such low aggregation rates when heated at high temperatures that they contribute strongly in improved the high-temperature strength of the deposited metal.
- the addition of tantalum to a com position which forms deposited metal containing not more than 5% ferrite is beneficial in avoiding welding crack and improving the corrosion resistance and hightemperature strength of the metal. Since the ferrite content of the deposited metal is too small for the formation of the sigma phase during heating at high temperatures, a good deposit can be obtained without any sacrifice of the corrosion resistance or hightemperature strength due to precipitation of the sigma phase.
- the amount of tantalum to be added is limited so that it accounts for 0.4 3.0% of the deposited metal.
- the lower limit of 0.4% is set for the reason now to be explained.
- the minimum amount of tantalum required for stabilizing carbon and producing tantalum carbide is C% X 15.
- C% X 20 or more is required because tantalum reacts with nitrogen and oxygen and accordingly the amount of tantalum that effectively combines with carbon is decreased. Since the minimum value of carbon content is approximately 0.02%, it follows that the minimum value of tantalum should be 0.02% X 20 0.4%.
- the upper limit of 3.0% is set because a higher percentage of tantalum would produce a brittle intermetallic compound TaFe, which in turn would embrittle the deposited metal and increase the crack sensitivity of the deposit.
- niobium in the deposited metal is restricted to 0.3% or less for the following reason.
- 0.3% or less niobium can have nothing to do with welding crack, but because Nb is difficult to separate from Ta the former gains entrance as an impurity element into the deposit, and the addition of more than 0.3% Nb would lead to formation of Nb-based low-melting-point foreign matter and cracking of the deposit owing to the heat of welding.
- the deposited metal formed in conformity with the invention contains tantalum preferably in the range between 0.4 and 3.0%.
- the ranges of other additivies must be fixed. Tantalum when added to at least either filler metal or flux as taught above is not totally carried into the deposited metal because it is oxidized and consumed during welding with partial transfer into the slag. These possible losses must be taken into account in determining the amount of tantalum to be added.
- the overall loss of an effective addition element in the course of welding depends upon the type of carrier in which it is added (i.e., in either filler metal or flux) and the method of welding to be adopted. Once these conditions are set, there will be practically no variation in the loss thenceforth.
- Ta When to be added to the flux (coating) alone Ta should range in amount from 0.8 to 30.0%.
- Ta proportions similar to those specified above will enable the welding material for submerged arc welding to form deposits as desirable as in shield arc welding.
- Ta added in an amount of 0.4 5.0% to the tiller metal will make possible the formation of a desired deposit.
- the grounds on which the composition of deposited metal is specified as above and the composition of the welding rod is so chosen as to obtain the particular deposit in accordance with this invention will now be clarified in connection with examples thereof.
- the electrode according to this invention gives a deposited metal having a lower crack sensitivity and better high-temperature strength and corrosion resistance than those of deposits formed by conventional electrodes of commerce.
- care must be used to avoid segregation.
- the element should be as fine in grain size as possible and should be uniformly distributed in the flux.
- imercrysml- 650C steel is drawn through a die into a wire form, and finecrate (65 c HNO;) line X1000 trade Cm/momh Corrosion hrs shed to a predetermined diameter.
- the w re finished in this way is cut to a suitable length and is used as a f 21in 0-0042 Good 25 bare filler metal for inert-gas welding or as a coated electrode with a suitable covering for the intended use.
- f Several examples of welding experimentally conzTf 71 00093 Fair to poor 19 ducted with filler metal s thus obtained are compared (2) 3 (in 0.0121 Fair to poor 13 with those conducted with conventional filler metals in Tables 3 and 4.
- Coated electrodes according to the invention are manufactured by applying a coating suitably prepared in view of the type of filler metal or of Next, a typical method of manufacturing an electhe welding conditions to be encountered over the filler trode in accordance with this invention will be demetal and then drying the coating.
- Filler metal of filler metal deposited metal C Si Mn Cr Ni Nb Ta C Si Mn Cr Ni Nb Ta 1 Conventional 0.045 0.54 1.60 18.51 10.55 0.72 0.031 0.52 1.58 17.92 10.52 0.52
- the end can be attained by coating the necessary number of core wires of ordinary austenitic stainless steel free from any additional element with a coating composition so prepared as to contain tantalum in the proportion specified above.
- An aqueous solution of sodium silicate is used as a binder.
- the electrodes with compositions to which tantalum is added in amounts within the range specified herein produce deposited metals superior in anticracking, anticorrosive, and high-temperature properties than the one formed with a conventional electrode and that the compositions with Ta contents outside the specified range give deposits inferior in resistance to cracking and corrosive attack.
- Table 3 shows the results of some inert-gas arc welding tests conducted with Ta-containing filler metals.
- filler metals of the invention were employed in welding steel of the DIN 4505 grade (conforming to DIN 17007 of the German standards) for anti-sulfuric acid use.
- Filler metals of DIN 4507 (DIN 17007), which are usually used for this purpose do not contain ferrite but do contain niobium in amounts of more than C% X 10 and naturally have the disadvantage of frequent cracking on welding.
- the properties of the deposited metals formed by the tiller metals of the invention were compared with those by the conventional filler metals. Table 6 shows the results of elementary analyses of deposited metals formed by inert-gas shielded arc welding with Ta-containing filler metals of the invention and with ordinary Ta-free ones.
- Table 7 compiles the test results obtained by the Methods of Type C,R estraint Welding Crack Test (JIS Z3155) and by the Methods of Copper-Containing Sulfuric Acid-Copper Sulfate Inter-crystalline Corrosion Test (JIS) and compares the mechanical properties of the deposited metals thus formed.
- inert-gas shielded arc welding with a filler metal that will allow the deposited metal to contain tantalum will thus form the deposited metal with improved resistance to cracking and intercrystalline corrosion and with high tensile strength.
- Ta is added to the deposited metal.
- the addition of less than 0.40% Ta will not be beneficial in improving the resistance to intercrystalline corrosion and more than 3.0% Ta will adversely affect the mechanical properties, particularly elongation, of the deposited metal.
- the Ta addition should be limited within the range of 0.40 to 3.0%.
- Nb contents of less than 0.30% have no effect on welding crack.
- a welding material is prepared in which tantalum is contained in such an amount that from 0.4 to 3.0% of the element is left in the deposited metal formed in the welding of austenitic stainless steels, and the material is added heforehand to at least either filler metal (including the core wire for shielded arc welding) or flux, and then shielded arc welding, inert-gas shielded arc welding, submerged arc welding, or the like is carried out to produce a deposited metal having excellent crack resistance, corrosion resistance, and high-temperature strength.
- the invention thus has great industrial advantages.
- the improvement which comprises either the core wire or coating of the electrode having an amount of Ta effective to produce a Ta content in the deposited metal of 0.40-3.0%.
- a core wire for welding austenitic stainless steels consisting essentially of not more than 0.15% C, 15.0 30.0% Cr, 8.0 20.0% Ni, not more than 2.5% Mn, not more than 0.9% Si, not more than 0.04% P, not more than 0.03% S, not more than 0.30% Nb, and 0.44 5.0% Ta, the balance being iron and incidental impurities.
Landscapes
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Nonmetallic Welding Materials (AREA)
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP6882672A JPS5516757B2 (de) | 1972-07-10 | 1972-07-10 | |
| JP6882772A JPS4927451A (de) | 1972-07-10 | 1972-07-10 | |
| JP7659372A JPS4934439A (de) | 1972-07-31 | 1972-07-31 |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| US3914506A true US3914506A (en) | 1975-10-21 |
Family
ID=27299865
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| US374966A Expired - Lifetime US3914506A (en) | 1972-07-10 | 1973-06-29 | Welding material for austenitic stainless steels |
Country Status (3)
| Country | Link |
|---|---|
| US (1) | US3914506A (de) |
| FR (1) | FR2191977B1 (de) |
| GB (1) | GB1440362A (de) |
Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5614149A (en) * | 1993-07-08 | 1997-03-25 | Nippon Yakin Kogyo Co., Ltd. | Stainless steels for coins and method of producing coins of stainless steel |
| US20120198685A1 (en) * | 2010-10-07 | 2012-08-09 | Aurecyl Dalla Bernardina Junior | Method to produce an electrode with a low level of hydrogen and low absorption of moisture |
| CN102699579A (zh) * | 2012-06-12 | 2012-10-03 | 中冶焊接科技有限公司 | 高铬镍全奥氏体不锈钢气保护焊接用药芯焊丝 |
| CN103659044A (zh) * | 2012-09-12 | 2014-03-26 | 昆山京群焊材科技有限公司 | T型co2气体保护高速角焊用串联双丝型组合焊丝 |
| CN104858572A (zh) * | 2015-03-31 | 2015-08-26 | 上海焊接器材有限公司 | 一种高铬铁素体不锈钢金属芯药芯焊丝 |
| CN112404794A (zh) * | 2020-10-08 | 2021-02-26 | 武汉科技大学 | 一种用于低氮无磁舰艇钢焊接的手工电弧焊焊条 |
| CN113352021A (zh) * | 2021-06-03 | 2021-09-07 | 西安热工研究院有限公司 | 一种铬镍奥氏体不锈钢焊接用的药芯焊丝及其制备方法 |
Families Citing this family (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS58125396A (ja) * | 1982-01-22 | 1983-07-26 | Hitachi Ltd | オ−ステナイト系溶接構造物 |
| FR2669645A1 (fr) * | 1990-11-22 | 1992-05-29 | Castolin Sa | Procede de preparation de couches de forte adherence. |
| US5389334A (en) * | 1993-04-22 | 1995-02-14 | Culling; John H. | Abrasion and corrosion resistant alloys |
| US5320801A (en) * | 1993-04-26 | 1994-06-14 | Carondelet Foundry Company | High carbon high chromium alloys having corrosion and abrasion resistance |
| US5360592A (en) * | 1993-07-22 | 1994-11-01 | Carondelet Foundry Company | Abrasion and corrosion resistant alloys |
| CN113001092B (zh) * | 2021-02-02 | 2023-01-06 | 中国水电四局（兰州）机械装备有限公司 | 一种六等分钢管加劲环组拼设备 |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US2801916A (en) * | 1954-08-24 | 1957-08-06 | Jessop William & Sons Ltd | Ferrous alloys for high temperature use |
| US2823114A (en) * | 1954-07-30 | 1958-02-11 | Babcock & Wilcox Co | Forgeable high strength austenitic alloy with columbium-tantalum addition |
| US2889223A (en) * | 1955-08-08 | 1959-06-02 | Electric Steel Foundry Co | Stainless steel alloy and method of forming |
| US3337331B1 (de) * | 1964-01-29 | 1967-08-22 |
Family Cites Families (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US3118761A (en) * | 1955-05-09 | 1964-01-21 | Westinghouse Electric Corp | Crack resistant austenitic stainless steel alloys |
-
1973
- 1973-06-29 US US374966A patent/US3914506A/en not_active Expired - Lifetime
- 1973-07-10 FR FR7325282A patent/FR2191977B1/fr not_active Expired
- 1973-07-10 GB GB3282373A patent/GB1440362A/en not_active Expired
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US2823114A (en) * | 1954-07-30 | 1958-02-11 | Babcock & Wilcox Co | Forgeable high strength austenitic alloy with columbium-tantalum addition |
| US2801916A (en) * | 1954-08-24 | 1957-08-06 | Jessop William & Sons Ltd | Ferrous alloys for high temperature use |
| US2889223A (en) * | 1955-08-08 | 1959-06-02 | Electric Steel Foundry Co | Stainless steel alloy and method of forming |
| US3337331B1 (de) * | 1964-01-29 | 1967-08-22 | ||
| US3337331A (en) * | 1964-01-29 | 1967-08-22 | Sandvikens Jernverks Ab | Corrosion resistant steel alloy |
Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5614149A (en) * | 1993-07-08 | 1997-03-25 | Nippon Yakin Kogyo Co., Ltd. | Stainless steels for coins and method of producing coins of stainless steel |
| US20120198685A1 (en) * | 2010-10-07 | 2012-08-09 | Aurecyl Dalla Bernardina Junior | Method to produce an electrode with a low level of hydrogen and low absorption of moisture |
| CN102699579A (zh) * | 2012-06-12 | 2012-10-03 | 中冶焊接科技有限公司 | 高铬镍全奥氏体不锈钢气保护焊接用药芯焊丝 |
| CN103659044A (zh) * | 2012-09-12 | 2014-03-26 | 昆山京群焊材科技有限公司 | T型co2气体保护高速角焊用串联双丝型组合焊丝 |
| CN103659044B (zh) * | 2012-09-12 | 2016-02-17 | 昆山京群焊材科技有限公司 | T型co2气体保护高速角焊用串联双丝型组合焊丝 |
| CN104858572A (zh) * | 2015-03-31 | 2015-08-26 | 上海焊接器材有限公司 | 一种高铬铁素体不锈钢金属芯药芯焊丝 |
| CN112404794A (zh) * | 2020-10-08 | 2021-02-26 | 武汉科技大学 | 一种用于低氮无磁舰艇钢焊接的手工电弧焊焊条 |
| CN113352021A (zh) * | 2021-06-03 | 2021-09-07 | 西安热工研究院有限公司 | 一种铬镍奥氏体不锈钢焊接用的药芯焊丝及其制备方法 |
Also Published As
| Publication number | Publication date |
|---|---|
| DE2335270B2 (de) | 1975-07-24 |
| FR2191977B1 (de) | 1976-11-12 |
| GB1440362A (en) | 1976-06-23 |
| FR2191977A1 (de) | 1974-02-08 |
| DE2335270A1 (de) | 1974-01-24 |
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