CN114932334B - Welding method of anode target plate - Google Patents
Welding method of anode target plate Download PDFInfo
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- CN114932334B CN114932334B CN202210669763.XA CN202210669763A CN114932334B CN 114932334 B CN114932334 B CN 114932334B CN 202210669763 A CN202210669763 A CN 202210669763A CN 114932334 B CN114932334 B CN 114932334B
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- 238000003466 welding Methods 0.000 title claims abstract description 86
- 238000000034 method Methods 0.000 title claims abstract description 74
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims abstract description 119
- 229910002804 graphite Inorganic materials 0.000 claims abstract description 119
- 239000010439 graphite Substances 0.000 claims abstract description 119
- 229910001182 Mo alloy Inorganic materials 0.000 claims abstract description 74
- 239000000843 powder Substances 0.000 claims abstract description 22
- 238000001465 metallisation Methods 0.000 claims abstract description 20
- 229910052723 transition metal Inorganic materials 0.000 claims abstract description 14
- 150000003624 transition metals Chemical class 0.000 claims abstract description 14
- 229910000045 transition metal hydride Inorganic materials 0.000 claims abstract description 12
- 238000007750 plasma spraying Methods 0.000 claims abstract description 9
- 238000002844 melting Methods 0.000 claims abstract description 5
- 230000008018 melting Effects 0.000 claims abstract description 5
- 238000005507 spraying Methods 0.000 claims abstract description 5
- 230000008569 process Effects 0.000 claims description 47
- 238000004381 surface treatment Methods 0.000 claims description 19
- 239000002245 particle Substances 0.000 claims description 15
- 229910000679 solder Inorganic materials 0.000 claims description 13
- -1 titanium hydride Chemical compound 0.000 claims description 6
- 229910000048 titanium hydride Inorganic materials 0.000 claims description 3
- QSGNKXDSTRDWKA-UHFFFAOYSA-N zirconium dihydride Chemical compound [ZrH2] QSGNKXDSTRDWKA-UHFFFAOYSA-N 0.000 claims description 3
- 229910000568 zirconium hydride Inorganic materials 0.000 claims description 3
- 150000004678 hydrides Chemical class 0.000 claims 1
- 229910052751 metal Inorganic materials 0.000 description 42
- 239000002184 metal Substances 0.000 description 42
- 239000002131 composite material Substances 0.000 description 32
- 238000012986 modification Methods 0.000 description 7
- 230000004048 modification Effects 0.000 description 7
- 238000005219 brazing Methods 0.000 description 6
- 238000010586 diagram Methods 0.000 description 5
- 230000008901 benefit Effects 0.000 description 4
- 230000004907 flux Effects 0.000 description 4
- 238000003754 machining Methods 0.000 description 4
- 238000009849 vacuum degassing Methods 0.000 description 4
- CPTCUNLUKFTXKF-UHFFFAOYSA-N [Ti].[Zr].[Mo] Chemical compound [Ti].[Zr].[Mo] CPTCUNLUKFTXKF-UHFFFAOYSA-N 0.000 description 3
- 238000004140 cleaning Methods 0.000 description 3
- 230000006872 improvement Effects 0.000 description 3
- 239000000463 material Substances 0.000 description 3
- 238000010008 shearing Methods 0.000 description 3
- 239000010936 titanium Substances 0.000 description 3
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 2
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 2
- QCWXUUIWCKQGHC-UHFFFAOYSA-N Zirconium Chemical compound [Zr] QCWXUUIWCKQGHC-UHFFFAOYSA-N 0.000 description 2
- 238000001816 cooling Methods 0.000 description 2
- OANFWJQPUHQWDL-UHFFFAOYSA-N copper iron manganese nickel Chemical compound [Mn].[Fe].[Ni].[Cu] OANFWJQPUHQWDL-UHFFFAOYSA-N 0.000 description 2
- 238000007872 degassing Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 239000007789 gas Substances 0.000 description 2
- 229910052735 hafnium Inorganic materials 0.000 description 2
- VBJZVLUMGGDVMO-UHFFFAOYSA-N hafnium atom Chemical compound [Hf] VBJZVLUMGGDVMO-UHFFFAOYSA-N 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 229910052739 hydrogen Inorganic materials 0.000 description 2
- 239000001257 hydrogen Substances 0.000 description 2
- 238000004519 manufacturing process Methods 0.000 description 2
- 239000007921 spray Substances 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- 229910052719 titanium Inorganic materials 0.000 description 2
- 229910052726 zirconium Inorganic materials 0.000 description 2
- 229910001339 C alloy Inorganic materials 0.000 description 1
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 1
- 229910000858 La alloy Inorganic materials 0.000 description 1
- 229910000691 Re alloy Inorganic materials 0.000 description 1
- MHHJYDUGLBFUSG-UHFFFAOYSA-N [C].[Hf].[Mo] Chemical compound [C].[Hf].[Mo] MHHJYDUGLBFUSG-UHFFFAOYSA-N 0.000 description 1
- CBPOHXPWQZEPHI-UHFFFAOYSA-N [Mo].[La] Chemical compound [Mo].[La] CBPOHXPWQZEPHI-UHFFFAOYSA-N 0.000 description 1
- 230000009471 action Effects 0.000 description 1
- 230000006978 adaptation Effects 0.000 description 1
- 238000000280 densification Methods 0.000 description 1
- 238000001514 detection method Methods 0.000 description 1
- 238000004880 explosion Methods 0.000 description 1
- 238000005087 graphitization Methods 0.000 description 1
- 150000002431 hydrogen Chemical class 0.000 description 1
- 239000012535 impurity Substances 0.000 description 1
- 230000001788 irregular Effects 0.000 description 1
- 239000003607 modifier Substances 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- 239000011733 molybdenum Substances 0.000 description 1
- YUSUJSHEOICGOO-UHFFFAOYSA-N molybdenum rhenium Chemical compound [Mo].[Mo].[Re].[Re].[Re] YUSUJSHEOICGOO-UHFFFAOYSA-N 0.000 description 1
- 238000004321 preservation Methods 0.000 description 1
- 230000002035 prolonged effect Effects 0.000 description 1
- 238000004088 simulation Methods 0.000 description 1
- 238000005476 soldering Methods 0.000 description 1
- 238000003860 storage Methods 0.000 description 1
- 230000001052 transient effect Effects 0.000 description 1
- 238000004506 ultrasonic cleaning 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
- B23K31/00—Processes relevant to this subclass, specially adapted for particular articles or purposes, but not covered by only one of the preceding main groups
- B23K31/02—Processes relevant to this subclass, specially adapted for particular articles or purposes, but not covered by only one of the preceding main groups relating to soldering or 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
- B23K2103/00—Materials to be soldered, welded or cut
- B23K2103/08—Non-ferrous metals or alloys
-
- 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
- B23K2103/00—Materials to be soldered, welded or cut
- B23K2103/50—Inorganic material, e.g. metals, not provided for in B23K2103/02 – B23K2103/26
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- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Coating By Spraying Or Casting (AREA)
- Arc Welding In General (AREA)
Abstract
The embodiment of the specification provides a welding method of an anode target disk, which comprises the following steps: spraying transition metal hydride powder on the surface to be welded of graphite in a plasma spraying mode to carry out metallization treatment on the graphite, wherein the plasma spraying temperature is higher than the melting point of transition metal in the transition metal hydride; and welding the metallized graphite and molybdenum alloy.
Description
Technical Field
The specification relates to the technical field of heterogeneous material connection, in particular to a welding method of graphite and molybdenum alloy in an anode target disk.
Background
The graphite/molybdenum alloy composite member has good thermal conductivity, and is widely used in the aerospace industry, biomedical engineering (for example, anode target disk for CT machine in medical diagnostic equipment), and the like. In order to meet the use requirements, graphite/molybdenum alloy composites are required to have high shear strength and interfacial bonding rate. Accordingly, there is a need to provide an improved welding process to increase the shear strength and interfacial bonding rate of graphite/molybdenum alloy composites.
Disclosure of Invention
One of the embodiments of the present specification provides a method of welding an anode target disk, the method comprising: spraying transition metal hydride powder on a graphite surface to be welded in a plasma spraying mode to carry out metallization treatment on the graphite, wherein the temperature of the plasma spraying is higher than the melting point of transition metal in the transition metal hydride; and welding the metallized graphite and molybdenum alloy.
In some embodiments, the method further comprises: and carrying out surface treatment on the graphite, wherein the graphite after the surface treatment forms a groove structure.
In some embodiments, the depth of the groove is in the range of 0.1mm-0.3 mm.
In some embodiments, the grooves have a width in the range of 0.05mm to 0.2 mm.
In some embodiments, the transition metal hydride comprises zirconium hydride, titanium hydride, or hafnium hydride.
In some embodiments, the particle size of the powder is in the range of 100 mesh to 1000 mesh.
In some embodiments, the metal layer formed after the metallization process has a thickness in the range of 50 μm to 300 μm.
In some embodiments, no pressure is applied during the welding process.
In some embodiments, the graphite is positioned above the molybdenum alloy during the welding process.
One of the embodiments of the present disclosure also provides an anode target disk, which is manufactured using the welding method of the anode target disk.
In some embodiments, the anode target disk has a room temperature shear strength in the range of 15MPa to 26 MPa.
In the embodiment of the specification, the groove structure with a certain depth and a certain width is formed by carrying out surface treatment on graphite, and further, the metallization treatment is carried out on the graphite on the basis of the groove structure, so that a metal layer with a certain thickness on the groove structure is formed. In the welding process of graphite and molybdenum alloy, the metal layer can serve as welding flux (no additional welding flux is needed in the corresponding welding process), and the groove structure can increase the bonding surface area of the graphite and the molybdenum alloy, so that the welding strength and the interface bonding rate of the composite part formed by welding are integrally improved on the basis of improving the production efficiency.
Drawings
The present specification will be further elucidated by way of example embodiments, which will be described in detail by means of the accompanying drawings. The embodiments are not limiting, in which like numerals represent like structures, wherein:
FIG. 1 is a flow chart of an exemplary welding method shown in accordance with some embodiments of the present description;
FIG. 2 is a schematic structural view of an exemplary surface treated graphite according to some embodiments of the present disclosure;
FIG. 3 is a schematic diagram of a structure of graphite after an exemplary metallization process according to some embodiments of the present description;
fig. 4 is a schematic diagram of an exemplary welding process according to some embodiments of the present description.
In the figure, 200 is graphite, 210 is a groove structure, 300 is a metal layer, and 400 is a molybdenum alloy.
Detailed Description
In order to more clearly illustrate the technical solutions of the embodiments of the present specification, the drawings that are required to be used in the description of the embodiments will be briefly described below. It is apparent that the drawings in the following description are only some examples or embodiments of the present specification, and it is possible for those of ordinary skill in the art to apply the present specification to other similar situations according to the drawings without inventive effort. Unless otherwise apparent from the context of the language or otherwise specified, like reference numerals in the figures refer to like structures or operations.
As used in this specification and the claims, the terms "a," "an," "the," and/or "the" are not specific to a singular, but may include a plurality, unless the context clearly dictates otherwise. In general, the terms "comprises" and "comprising" merely indicate that the steps and elements are explicitly identified, and they do not constitute an exclusive list, as other steps or elements may be included in a method or apparatus.
FIG. 1 is a flow chart of an exemplary welding method shown in accordance with some embodiments of the present description. In some embodiments, the process 100 may be performed by processing logic that may comprise hardware (e.g., circuitry, dedicated logic, programmable logic, microcode, etc.), software (instructions run on a processing device to perform hardware simulation), or the like, or any combination thereof. One or more operations in the flow 100 of the welding method shown in fig. 1 may be implemented by a processing device. For example, the process 100 may be stored in the storage device in the form of instructions and executed by the processing device to invoke and/or execute.
As shown in fig. 1, the process 100 may include the following steps.
At step 110, the graphite is surface treated.
In some embodiments, the surface to be welded of graphite may be surface treated. In some embodiments, the surface treatment may increase the surface area of the surface to be soldered. By effectively increasing the surface area of the surface to be welded, the interface bonding area between graphite and molybdenum alloy in the subsequent welding process can be increased, and the welding strength and the interface bonding rate of the graphite/molybdenum alloy composite part can be correspondingly improved.
In some embodiments, the surface treated graphite may form a fluted structure. In some embodiments, the cross-section of the groove structure may include, but is not limited to, any regular or irregular shape including polygonal, hemispherical, semi-elliptical, etc. For example triangular, rectangular, trapezoidal. Fig. 2 is a schematic structural diagram of an exemplary surface treated graphite according to some embodiments of the present disclosure. As shown in fig. 2, the cross-section of the groove structure 210 formed by surface treating the graphite 200 is triangular.
In some embodiments, the depth (shown as d in fig. 2) and/or width (shown as b in fig. 2) of the groove can affect the shear strength and interfacial bonding rate of the graphite/molybdenum alloy composite member. For example, too small a depth or width of the groove may not effectively increase the area of the graphite to be welded, resulting in a lower interfacial bonding rate of the graphite/molybdenum alloy composite, and a lower weld strength of the graphite and molybdenum alloy, and thus a lower shear strength of the graphite/molybdenum alloy composite. As another example, too large a depth or width of the groove may result in a lower interfacial bonding rate (or greater porosity) of the graphite/molybdenum alloy composite. Thus, in some embodiments, the depth and/or width of the grooves need to be within a predetermined range.
In some embodiments, the depth of the grooves may be in the range of 0.1mm-0.3 mm. In some embodiments, the depth of the grooves may be in the range of 0.12mm-0.28 mm. In some embodiments, the depth of the grooves may be in the range of 0.14mm-0.26 mm. In some embodiments, the depth of the grooves may be in the range of 0.16mm-0.24 mm. In some embodiments, the depth of the grooves may be in the range of 0.18mm-0.22 mm. In some embodiments, the depth of the grooves may be in the range of 0.19mm-0.2 mm.
In some embodiments, the width of the groove may be in the range of 0.05mm-0.2 mm. In some embodiments, the width of the groove may be in the range of 0.07mm-0.18 mm. In some embodiments, the width of the groove may be in the range of 0.09mm-0.16 mm. In some embodiments, the width of the groove may be in the range of 0.11mm-0.14 mm. In some embodiments, the width of the groove may be in the range of 0.12mm-0.13 mm.
In some embodiments, the surface treatment may increase the area of the surface to be welded by in the range of 50% -150%. In some embodiments, the surface treatment may increase the area of the surface to be welded by in the range of 60% -140%. In some embodiments, the surface treatment may increase the area of the surface to be welded by in the range of 70% -130%. In some embodiments, the surface treatment may increase the area of the surface to be welded by 80% -120%. In some embodiments, the surface treatment may increase the area of the surface to be welded by a range of 90% -110%. In some embodiments, the surface treatment may increase the area of the surface to be welded by a range of 100% -110%.
In some embodiments, the graphite may be surface treated by laser machining or machining, or the like. The laser machining or machining process is more efficient and the resulting surface structure (e.g., groove structure) is more accurate than the surface treatment of graphite by sanding or the like, either manually or in a rough manner.
In the embodiment of the specification, the surface treatment is performed on the graphite, so that the welding combination area of the graphite and the molybdenum alloy can be increased, the welding strength of the graphite and the molybdenum alloy is increased, and the shearing strength of the graphite/molybdenum alloy composite part is improved. In addition, the shear strength and interfacial bonding rate may be further ensured by the definition of parameters of the surface treatment (e.g., increased area of the surface to be welded, depth and/or width of the groove).
And 120, spraying transition metal hydride powder on the surface to be welded of the graphite in a plasma spraying mode so as to carry out metallization treatment on the graphite.
In some embodiments, a metal layer may be formed to a certain thickness after the metallization process. Specifically, after metallization treatment, metal is filled in the groove structure of the graphite surface to be welded, and a metal layer with a certain thickness is formed. For example, fig. 3 is a schematic structural diagram of an exemplary metallized graphite according to some embodiments of the present disclosure. As shown in fig. 3, the molten transition metal may be filled in the groove structure 210 of the surface to be welded of the graphite 200, and form a metal layer 300 on the surface to be welded of the graphite 200. In the subsequent welding process, the metal layer can be used as solder, and accordingly, no additional solder is required to be added, so that the welding process can be simplified, and the welding efficiency can be improved.
In some embodiments, the transition metal hydrides may include, but are not limited to, zirconium hydride, titanium hydride, hafnium hydride, and the like. A transient high temperature is formed during plasma spraying of the powder, which may be above the melting point of the transition metal in the transition metal hydride. For example, zirconium may have a melting point of about 1855 ℃, titanium about 1668 ℃, hafnium about 2233 ℃, and plasma spray temperatures may be higher than 1855 ℃, 1668 ℃ or 2233 ℃, respectively. In the spraying process, the transition metal hydride can be decomposed, hydrogen is formed by hydrogen, and the transition metal is deposited on the surface to be welded of graphite in a molten state to form a metal layer. The chemical binding force (for example, transition metal carbide formed by graphite and transition metal) exists between the metal layer and the graphite surface to be welded, so that the welding strength of the molybdenum alloy and the graphite in subsequent welding can be improved.
According to the embodiment of the specification, the metal graphitization treatment is realized at the instant high temperature formed by plasma spraying, so that the time of the graphite metallization treatment can be shortened, the efficiency of the graphite metallization treatment is improved, the metallization treatment is not required to be carried out in a furnace, and the operation can be simplified.
In some embodiments, the use of transition metal hydrides as the spray powder may avoid explosions that may result from excessive activity of the transition metal simple substance.
In some embodiments, the particle size of the powder can affect the quality (e.g., density, purity) of the metal layer, which in turn affects the shear strength of the graphite/molybdenum alloy composite. For example, too small a particle size of the powder may result in poor densification of the metal layer, which in turn may result in a lower weld strength of the graphite to the molybdenum alloy. As another example, too large a particle size of the powder can result in uneven or rough metal layers, which in turn can affect the subsequent welding process. Thus, in some embodiments, the particle size of the powder needs to be within a predetermined range.
In some embodiments, the particle size of the powder may be in the range of 100 mesh to 1000 mesh. In some embodiments, the particle size of the powder may be in the range of 100 mesh to 900 mesh. In some embodiments, the particle size of the powder may be in the range of 100 mesh to 800 mesh. In some embodiments, the particle size of the powder may be in the range of 150 mesh to 750 mesh. In some embodiments, the particle size of the powder may be in the range of 200 mesh to 700 mesh. In some embodiments, the particle size of the powder may be in the range of 250 mesh to 650 mesh. In some embodiments, the particle size of the powder may be in the range of 300 mesh to 600 mesh. In some embodiments, the particle size of the powder may be in the range of 350 mesh to 550 mesh. In some embodiments, the particle size of the powder may be in the range of 400 mesh to 500 mesh.
In some embodiments, the metal layer thickness (as shown in fig. 3 h) can affect the shear strength of the graphite/molybdenum alloy composite and the subsequent welding process. For example, too small a metal layer thickness can result in too thin a weld layer for subsequent welding processes, which in turn can result in lower shear strength of the graphite/molybdenum alloy composite; in addition, if the thickness of the metal layer is too small, the metal layer cannot provide sufficient solder, and in this case, additional solder is required to be added, resulting in more complicated soldering process. As another example, excessive metal layer thickness may weaken the action of the groove structure or reduce the shear strength of the graphite/molybdenum alloy composite. Thus, in some embodiments, the metal layer thickness needs to be within a predetermined range.
In some embodiments, the metal layer thickness may be in the range of 50 μm-300 μm. In some embodiments, the metal layer thickness may be in the range of 80 μm-280 μm. In some embodiments, the metal layer thickness may be in the range of 100 μm-250 μm. In some embodiments, the metal layer thickness may be in the range of 120 μm-220 μm. In some embodiments, the metal layer thickness may be in the range of 150 μm-200 μm. In some embodiments, the metal layer thickness may be in the range of 160 μm-180 μm.
The welding surface of the graphite is subjected to metallization treatment (the formed metal layer is used as welding flux in the subsequent welding process), so that the wettability between the welding flux and the graphite and the welding strength between the graphite and the molybdenum alloy are improved, the shearing strength and the interfacial bonding rate of the welding layer or the graphite/molybdenum alloy composite part are further improved, the stability of the graphite/molybdenum alloy composite part is improved, and the service life of the graphite/molybdenum alloy composite part is prolonged.
In some embodiments, the process 100 may further include degassing (e.g., vacuum degassing) the surface treated graphite and molybdenum alloy prior to the metallization. Impurity gas in graphite and molybdenum alloy can be removed through degassing treatment, and air holes are avoided being formed in the subsequent welding process.
In some embodiments, the vacuum degassing treatment may include placing the surface treated graphite and molybdenum alloy in a vacuum furnace, heating to a predetermined temperature at a predetermined rate, maintaining the temperature for a certain period of time, and cooling with the furnace. By way of example only, the surface treated graphite and molybdenum alloy may be placed in a vacuum furnace, raised to 1300-1600 ℃ at a heating rate of 5-7 ℃/min, then incubated for 60-120 min, and then cooled to a temperature below 70 ℃ with the furnace.
In some embodiments, the vacuum level of the vacuum degassing process may be no greater than a predetermined value (e.g., 5 x 10 -4 Pa、4*10 -4 Pa、3*10 -4 Pa、2*10 -4 Pa、1*10 -4 Pa)。
In some embodiments, the process 100 may further include a cleaning process of the surface treated graphite and molybdenum alloy prior to the vacuum degassing process. In some embodiments, the cleaning process may include, but is not limited to, ultrasonic cleaning, gas phase cleaning.
And 130, performing welding treatment on the graphite and the molybdenum alloy after the metallization treatment.
In some embodiments, the mass percent of molybdenum element in the molybdenum alloy may be not less than 80%. In some embodiments, the molybdenum alloy may include, but is not limited to, TZM (titanium zirconium molybdenum alloy), MHC (molybdenum hafnium carbon alloy), ML (molybdenum lanthanum alloy), MRe (molybdenum rhenium alloy).
In some embodiments, the welding process may include, but is not limited to, brazing (e.g., vacuum brazing). As described above, in the welding process, the groove structure can increase the interface bonding area of graphite and molybdenum alloy, and the metal layer can be used as solder, so as to effectively increase the wettability between graphite and molybdenum alloy and improve the welding strength.
The pressure of the welding process includes the weight of the part to be welded (e.g., graphite) above the weld layer and the additional applied welding pressure. In some embodiments, no additional welding pressure is required during the welding process (e.g., brazing), which not only simplifies the welding process, but also allows for simultaneous welding of multiple graphite/molybdenum alloys and increases production efficiency.
In some embodiments, the welding process may include stacking graphite over and over the molybdenum alloy, placing the graphite face to be welded in contact with the molybdenum alloy face to be welded, and placing the graphite face in a welding furnace (e.g., a vacuum brazing furnace) to perform the welding operation, followed by furnace cooling. For example only, the welding temperature may be in the range of 1550 ℃ -1700 ℃, the hold time may be 10min-30min, and then furnace cooled to a temperature below 70 ℃.
In some embodiments, the vacuum of the welding process may be 1 x 10 -4 Pa-3*10 -3 In the Pa range. In some embodiments, the vacuum of the welding process may be at 3 x 10 -4 Pa-2*10 -3 In the Pa range. In some embodiments, the vacuum of the welding process may be at 5 x 10 -4 Pa-1*10 -3 In the Pa range.
In some embodiments, graphite may be located over the molybdenum alloy during the welding process. Because the graphite density is low, the graphite is positioned above the molybdenum alloy, so that not only can the welding pressure be reduced, but also the amount of solder (metal layer) overflowed during the welding treatment can be reduced. For example zirconium, titanium, hafnium.
Fig. 4 is a schematic diagram of an exemplary welding process according to some embodiments of the present description. As shown in fig. 4, the graphite 200 is positioned above the molybdenum alloy 400, and the upper and lower surfaces of the metal layer 300 formed by the metallization are in contact with the graphite 200 and the molybdenum alloy 400, respectively.
Ultrasonic flaw detection and mechanical property test are respectively carried out on the graphite/molybdenum alloy composite piece obtained after welding treatment in the embodiment of the specification, and the result shows that the interface bonding rate of the graphite/molybdenum alloy composite piece is not less than 95%, and the room temperature shear strength is in the range of 15-26 MPa. Accordingly, the room temperature shear strength of the anode target disk manufactured by the welding method is in the range of 15MPa-26 MPa.
It should be noted that the above description of the process 100 is for illustration and description only, and is not intended to limit the scope of applicability of the present disclosure. Various modifications and changes to the process 100 will be apparent to those skilled in the art in light of the present description. However, such modifications and variations are still within the scope of the present description. For example, the molybdenum alloy may be replaced by elemental molybdenum. For example, when the thickness of the metal layer is slightly insufficient, a certain amount of extra solder can be paved between the graphite surface to be welded and the molybdenum alloy surface to be welded after the metallization treatment, and the welding effect is improved.
Example 1
For a density of not less than 1.85g/cm 3 And carrying out surface treatment on graphite with ash content not more than 20ppm to obtain a groove structure with a triangular cross section (shown in figure 2). The depth d of the groove was 0.15mm and the width b of the groove was 0.1mm.
And (3) carrying out metallization treatment on the surface-treated graphite surface to be welded by adopting ZrH powder with the purity of not less than 99% and the granularity of 400 meshes to obtain the metal layer with the thickness of 50 mu m.
And (3) placing the metallized graphite above TZM (titanium zirconium molybdenum alloy), and carrying out vacuum brazing treatment without additionally applying welding pressure in the welding process to obtain the graphite/molybdenum alloy composite part. Wherein, the Ti content in TZM (titanium zirconium molybdenum alloy) is 0.4% -0.55%, the Zr content is 0.12% -0.66%, the C content is 0.01% -0.04%, and the balance is Mo. The brazing temperature is 1600 ℃, and the heat preservation time is 20min.
Example 2
The difference from example 1 is that the thickness of the metal layer is 100 μm.
Example 3
The difference from example 1 is that the thickness of the metal layer is 150 μm.
Example 4
The difference from example 1 is that the thickness of the metal layer is 200 μm.
Example 5
The difference from example 1 is that the thickness of the metal layer is 300 μm.
Example 6
The difference from example 1 is that the graphite was not surface-treated.
Example 7
The difference from example 2 is that the graphite was not surface-treated.
Example 8
The difference from example 3 is that the graphite was not surface-treated.
Example 9
The difference from example 5 is that the graphite was not surface-treated.
The graphite/molybdenum alloy composites obtained in examples 1 to 5 were examined, and the results are shown in Table 1.
Table 1 table of properties of graphite/molybdenum alloy composites of examples 1-5
| Thickness of metal layer/μm | Room temperature shear strength/MPa | Interfacial binding rate/% | |
| Example 1 | 50 | 20 | ≥95 |
| Examples2 | 100 | 23 | ≥95 |
| Example 3 | 150 | 26 | ≥95 |
| Example 4 | 200 | 23 | ≥95 |
| Example 5 | 300 | 20 | ≥95 |
The graphite/molybdenum alloy composites obtained in examples 6 to 9 were examined and the results are shown in Table 2.
Table 2 table of properties of graphite/molybdenum alloy composites of example 6-example 9
| Thickness of metal layer/μm | Room temperature shear strength/MPa | Interfacial binding rate/% | |
| Example 6 | 50 | 15 | ≥95 |
| Example 7 | 100 | 18 | ≥95 |
| Example 8 | 150 | 21 | ≥95 |
| Example 9 | 300 | 16 | ≥95 |
As can be seen from tables 1 and 2, the welding method of the examples of the present specification can obtain graphite/molybdenum alloy composite members having high shear strength (room temperature shear strength of 15MPa to 26 MPa) and high interfacial bonding rate (not less than 95%). Compared with a graphite/molybdenum alloy composite member obtained by carrying out surface treatment on graphite, the room-temperature shear strength of the graphite/molybdenum alloy composite member obtained by carrying out surface treatment on graphite can be increased by 23.8% -33.33%.
Possible benefits of embodiments of the present description include, but are not limited to: (1) The surface treatment of the graphite can increase the welding area of the graphite and the molybdenum alloy, thereby increasing the welding strength of the graphite and the molybdenum alloy and improving the shearing strength of the graphite/molybdenum alloy composite part; (2) The wettability between the solder and the graphite and between the solder and the molybdenum alloy can be improved by carrying out metallization treatment on the graphite, so that the welding strength of the graphite and the molybdenum alloy is improved, and the shear strength and the interfacial bonding rate of a welding layer or a graphite/molybdenum alloy composite part are further improved, thereby improving the stability of the graphite/molybdenum alloy composite part and prolonging the service life of the graphite/molybdenum alloy composite part; (3) The metal layer with preset thickness can be formed by carrying out metallization treatment on the graphite, the metal layer can be used as solder, and extra solder is not required to be added in the subsequent welding treatment process, so that the welding process can be simplified; (4) In the welding treatment process, graphite is positioned above the molybdenum alloy, so that the welding pressure can be reduced, and the overflow amount of solder (metal layer) in the welding treatment can be reduced; (5) The welding method of the embodiment of the specification can be used for obtaining the graphite/molybdenum alloy composite part with high shear strength (the room temperature shear strength is 15-26 MPa) and high interface bonding rate (not less than 95%).
It should be noted that, the advantages that may be generated by different embodiments may be different, and in different embodiments, the advantages that may be generated may be any one or a combination of several of the above, or any other possible advantages that may be obtained.
While the basic concepts have been described above, it will be apparent to those skilled in the art that the foregoing detailed disclosure is by way of example only and is not intended to be limiting. Although not explicitly described herein, various modifications, improvements, and adaptations to the present disclosure may occur to one skilled in the art. Such modifications, improvements, and modifications are intended to be suggested within this specification, and therefore, such modifications, improvements, and modifications are intended to be included within the spirit and scope of the exemplary embodiments of the present invention.
Meanwhile, the specification uses specific words to describe the embodiments of the specification. Reference to "one embodiment," "an embodiment," and/or "some embodiments" means that a particular feature, structure, or characteristic is associated with at least one embodiment of the present description. Thus, it should be emphasized and should be appreciated that two or more references to "an embodiment" or "one embodiment" or "an alternative embodiment" in various positions in this specification are not necessarily referring to the same embodiment. Furthermore, certain features, structures, or characteristics of one or more embodiments of the present description may be combined as suitable.
Likewise, it should be noted that in order to simplify the presentation disclosed in this specification and thereby aid in understanding one or more inventive embodiments, various features are sometimes grouped together in a single embodiment, figure, or description thereof. This method of disclosure, however, is not intended to imply that more features than are presented in the claims are required for the present description. Indeed, less than all of the features of a single embodiment disclosed above.
In some embodiments, numbers describing the components, number of attributes are used, it being understood that such numbers being used in the description of embodiments are modified in some examples by the modifier "about," approximately, "or" substantially. Unless otherwise indicated, "about," "approximately," or "substantially" indicate that the number allows for a 20% variation. Accordingly, in some embodiments, numerical parameters set forth in the specification and claims are approximations that may vary depending upon the desired properties sought to be obtained by the individual embodiments. In some embodiments, the numerical parameters should take into account the specified significant digits and employ a method for preserving the general number of digits. Although the numerical ranges and parameters set forth herein are approximations that may be employed in some embodiments to confirm the breadth of the range, in particular embodiments, the setting of such numerical values is as precise as possible.
Each patent, patent application publication, and other material, such as articles, books, specifications, publications, documents, etc., referred to in this specification is incorporated herein by reference in its entirety. Except for application history documents that are inconsistent or conflicting with the content of this specification, documents that are currently or later attached to this specification in which the broadest scope of the claims to this specification is limited are also. It is noted that, if the description, definition, and/or use of a term in an attached material in this specification does not conform to or conflict with what is described in this specification, the description, definition, and/or use of the term in this specification controls.
Finally, it should be understood that the embodiments described in this specification are merely illustrative of the principles of the embodiments of this specification. Other variations are possible within the scope of this description. Thus, by way of example, and not limitation, alternative configurations of embodiments of the present specification may be considered as consistent with the teachings of the present specification. Accordingly, the embodiments of the present specification are not limited to only the embodiments explicitly described and depicted in the present specification.
Claims (10)
1. A method of welding an anode target disk, the method comprising:
spraying the hydride powder of the transition metal on the surface to be welded of the graphite in a plasma spraying mode to metalize the graphite to form carbide of the transition metal and the transition metal layer with preset thickness, wherein,
the transition metal layer is used as solder;
the temperature of the plasma spraying is higher than the melting point of the transition metal in the transition metal hydride;
and welding the metallized graphite and molybdenum alloy.
2. The method of welding an anode target disk of claim 1, further comprising: and carrying out surface treatment on the graphite, wherein the graphite after the surface treatment forms a groove structure.
3. The method of welding an anode target disk according to claim 2, wherein the depth of the groove is in the range of 0.1mm to 0.3mm, and the width of the groove is in the range of 0.05mm to 0.2 mm.
4. The method of claim 1, wherein the transition metal hydride comprises zirconium hydride, titanium hydride, or hafnium hydride.
5. The method of welding an anode target disk according to claim 1, wherein the particle size of the powder is in the range of 100 mesh to 1000 mesh.
6. The method of claim 1, wherein the thickness of the transition metal layer formed after the metallization is in the range of 50 μm to 300 μm.
7. The method of claim 1, wherein no additional welding pressure is applied during the welding process.
8. The method of claim 1, wherein the graphite is positioned above the molybdenum alloy during the welding process.
9. An anode target disk, characterized in that it is manufactured by using the welding method of the anode target disk according to any one of claims 1 to 8.
10. The anode target disk of claim 9, wherein the anode target disk has a room temperature shear strength in the range of 15MPa to 26 MPa.
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