CN104404307A - Nickel-based alloy interface layer, and its new TLP welding high temperature alloy technology - Google Patents
Nickel-based alloy interface layer, and its new TLP welding high temperature alloy technology Download PDFInfo
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- CN104404307A CN104404307A CN201410593770.1A CN201410593770A CN104404307A CN 104404307 A CN104404307 A CN 104404307A CN 201410593770 A CN201410593770 A CN 201410593770A CN 104404307 A CN104404307 A CN 104404307A
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Abstract
The invention discloses a nickel-based alloy interface layer for TLP welding. The interface layer comprises 3.2-3.5% of B, 2.4-3% of Si, 0.2-0.4% of Nd, 3-4% of Co, 1-2% of Cr, 2.5-3% of W, 1.2-2% of Ti, 1.5-2.5% of Al, 2-3% of Mo, and the balance of Ni, and the total percentage of the above atoms is 100%. The invention also discloses an application method of the interface layer alloy in TLP welding-solid solution heat treatment. The interface layer alloy can be applied in the TLP welding-heat treatment in order to greatly reduce the heat treatment time, save energy, reduce emission and greatly reduce the making cost.
Description
Technical field
The invention belongs to technical field of welding materials, relate to a kind of Nickel-base Alloy Interlayer for TLP weldering, the invention still further relates to and a kind ofly use the application method of this Nickel-base Alloy Interlayer in TLP weldering-solution heat treatment.
Background technology
Nickel base superalloy has good thermostability, heat resistance and high temperature microstructure stability, has become the critical material of Aeronautics and Astronautics engine turbine blade.The multiplex nickel base superalloy preparation of High Performance Aeroengine blade, and be often designed to hollow structure, to adapt to bear high-temperature alternate load and heat radiation needs.The manufacture of this complicated hollow structure inevitably relates to Welding Problems, and need carry out postweld heat treatment, and the production cycle is long, and energy consumption is large.
The chemical composition of nickel base superalloy is very complicated, and nickel content is greater than 50% usually, wherein adds multiplely to form heat-resisting strengthening phase element and phase stable element.Chromium, as phase stability element, forms dense oxidation film at alloy surface, can put forward heavy alloyed resistance of oxidation.By adding the alloying elements such as aluminium, titanium, cobalt, tungsten, molybdenum, tantalum, niobium, hafnium, produce the hot strength that solution strengthening, second-phase strength and grain-boundary strengthening realize alloy.Therefore, superalloy melting easily produces weld seam thermal crack, and soldering joint strength is low and resistance to elevated temperatures is poor.It is transition liquid phase diffusion weld that TLP welds full name, and TLP weldering has the convenience of soldering processes and the high performance characteristics of melting welding metallurgical binding concurrently, is the effective ways realizing nickel base superalloy welding.Middle layer alloying constituent is comparatively large on the impact of TLP welding joint Microstructure and properties, and in addition, welding process and follow-up thermal treatment process butt junction performance also have important impact.
Summary of the invention
The object of this invention is to provide a kind of Nickel-base Alloy Interlayer for TLP weldering, solve the problem that the welding joint Microstructure and properties existed in prior art can not meet technical requirements.
Another object of the present invention is to provide and a kind ofly uses the application method of this Nickel-base Alloy Interlayer in TLP weldering-solution heat treatment, namely uses this middle layer alloy to weld nickel base superalloy at TLP, the application taken into account in postwelding solution heat treatment.
The technical solution adopted in the present invention is, a kind of Nickel-base Alloy Interlayer for TLP weldering, by atomic percent, composed of the following components: B is 3.2%-3.5%, Si be 2.4%-3%, Nd be 0.2%-0.4%, Co be 3%-4%, Cr be 1%-2%, W be 2.5%-3%, Ti be 1.2%-2%, Al be 1.5%-2.5%, Mo is 2%-3%, surplus is Ni, and total per-cent is 100%.
Another technical scheme of the present invention is, a kind ofly use the application method of above-mentioned Nickel-base Alloy Interlayer in TLP weldering-solution heat treatment, first this middle layer fast chilling technique of Alloyapplication list roller is made as middle layer alloy foil, again middle layer alloy foil is placed between two nickel base superalloy samples to be welded, then according to TLP soldering method, the joint assembled heated, be incubated and slow cooling, thus realize the welding between nickel base superalloy.
The invention has the beneficial effects as follows, this is used for the Nickel-base Alloy Interlayer of TLP weldering, has excellent intensity, toughness and erosion resistance, and solidus curve and the liquidus line temperature difference are less, good with mother metal Performance Match, is easy to the welding joint of acquisition excellent high temperature performance; Soft alloy ductility can be good, is convenient to processing and assembling.This middle layer preparation method is simple, and easily operate, cost of manufacture is low.
This TLP weldering-thermal treatment integral method, greatly reduce heat treatment time, energy-saving and emission-reduction, manufacturing cost significantly reduces.
Accompanying drawing explanation
Fig. 1 is the code of the superalloy TLP weldering-solution heat treatment of the inventive method embodiment.
Embodiment
Below in conjunction with the drawings and specific embodiments, the present invention is described in detail.
Nickel-base Alloy Interlayer of the present invention, for welding nickel base superalloy in TLP method, composed of the following components by atomic percent: B is 3.2%-3.5%, Si be 2.4%-3%, Nd be 0.2%-0.4%, Co be 3%-4%, Cr be 1%-2%, W be 2.5%-3%, Ti be 1.2%-2%, Al be 1.5%-2.5%, Mo is 2%-3%, surplus is Ni, and total per-cent is 100%.
In Nickel-base Alloy Interlayer composition of the present invention, each component and content limit reason and are:
For the welding joint that acquisition Microstructure and properties and base metals match, the element kind contained by the alloy of middle layer should be similar to matrix constituent or close.TLP welds in superalloy middle layer containing elements such as W, Cr, Co, Mo, Nd, Ti and Al.In addition, the carrying out of welding process must be diffused as prerequisite with element, and the melting point depressant in middle layer must have both the fast characteristic of velocity of diffusion.B, Si, Nd etc. are as melting point depressant main in component, and wherein, the effect of B is best, and the atomic size of Si and Nd element is comparatively large, and diffusion is comparatively slow, and effect is taken second place.The determination of alloying element content, except meeting the performance matching requirements of weld seam and mother metal, also should consider alloying element and fall the interaction between molten, diffuse elements.
The preparation method of the invention described above middle layer alloy is, utilize vacuum arc fumace to melt successively and join master alloy and mother alloy, again the mother alloy through high-frequency induction melting being prepared into thickness on single roller rapid solidification device is 30-80 μm, wide is 5-8mm, the long middle layer alloy foil for 1-2m.
Adopt middle layer of the present invention alloy foil, by TLP method welding nickel base superalloy sample, in accordance with the following methods with the enforcement of step in TLP weldering-solution heat treatment (TLP welds and realizes homogenizing thermal treatment):
First middle layer alloy foil is placed between two nickel base superalloy samples to be welded, then according to TLP soldering method, the joint assembled is heated, be incubated and slow cooling, thus realize the welding between nickel base superalloy.
With reference to Fig. 1, be the code of the inventive method in superalloy TLP weldering-solution treatment process, a, c, e, g section is the constant-speed heating stage, and heating rate is 10 DEG C/min; B section is holding stage, namely at 1000 DEG C of insulation 30min; D section is the isothermal solidification stage, namely at 1200 DEG C of insulation 6h; F section is holding stage, namely at 1290 DEG C of insulation 3-5h; H section is holding stage, at 1315 DEG C of insulation 5h; I section is the air cooling stage.This curve is an embodiment curve.
TLP weldering-solution heat treatment the parameter of nickel base superalloy is: welding temperature 1200 ± 5 DEG C, soaking time 4-6h (i.e. d section); Postwelding is warmed up to 1290 ± 5 DEG C of insulations 3-5h (i.e. f section); Then continue to be warming up to 1315 ± 5 DEG C, and in this insulation 6-8h (i.e. h section); Welding pressure 0.2-0.5MPa, vacuum tightness 5 × 10-2Pa.Heating schedule is wherein: be heated to 1000 DEG C with the heat-up rate of 10 DEG C/min, insulation 30min; Welding temperature 1200 ± 5 DEG C, after being incubated setting-up time, again heat up, be incubated and air cooling to room temperature.
The TLP weldering using middle layer of the present invention alloy foil to carry out superalloy once completes with postwelding solution heat treatment process, and under existing weldprocedure operational condition, addition of the even process of diffusion, technique is simple, easy to operate, process simplification, and efficiency improves.Especially weldprocedure is stablized, and welding quality is easy to ensure, joint performance is promoted.
Each component in table 1, present method embodiment 1-5 and containing scale
Embodiment 1
Data according to embodiment in table 11 weigh the high pure metal content of each component, and application vacuum arc fumace is molten joins master alloy and mother alloy, and it is 40 μm that the fast chilling of single roller obtains thickness, and wide is 6mm, the long middle layer alloy foil for 1.5m.
The fusing point of the present embodiment 1 preparation-obtained middle layer alloy is 1069-1074 DEG C.This middle layer alloy foil is applied to the TLP welding of DD6 nickel-base high-temperature single crystal alloy sample, welding condition is: welding temperature 1200 DEG C, soaking time 5h; Postwelding is warmed up to 1290 DEG C of insulation 3h; Then continue to be warming up to 1315 DEG C, and at this insulation 6h; Welding pressure 0.2-0.5MPa, vacuum tightness 5 × 10
-2pa.Heating schedule is: be heated to 1000 DEG C with the heat-up rate of 10 DEG C/min, insulation 30min; Welding temperature 1200 DEG C, after being incubated setting-up time, again heat up, be incubated and air cooling to room temperature, with reference to shown in Fig. 1.
Welding joint structure and the mother metal matching of acquisition are good, and weld seam is single crystal forms tissue.
Embodiment 2
Data according to embodiment in table 12 weigh the high pure metal content of each component, and application vacuum arc fumace is molten joins master alloy and mother alloy, and it is 50 μm that the fast chilling of single roller obtains thickness, and wide is 5mm, the long middle layer alloy foil for 2m.
The fusing point of the present embodiment 2 preparation-obtained middle layer alloy is 1071-1077 DEG C.This middle layer alloy foil is applied to the TLP welding of DD3 nickel base superalloy sample, welding condition is: welding temperature 1200 DEG C, soaking time 4.5h; Postwelding is warmed up to 1290 DEG C of insulation 4h; Then continue to be warming up to 1315 DEG C, and at this insulation 7h; Welding pressure 0.2-0.5MPa, vacuum tightness 5 × 10
-2pa.Heating schedule is: be heated to 1000 DEG C with the heat-up rate of 10 DEG C/min, insulation 30min; Welding temperature 1200 DEG C, after being incubated setting-up time, again heat up, be incubated and air cooling to room temperature, with reference to shown in Fig. 1.
Welding joint structure and the mother metal matching of acquisition are good.
Embodiment 3
According to the step of above-described embodiment 1, the data according to embodiment in table 13 weigh the high pure metal of each component concentration, and preparing thickness is 60 μm, the quick cooling alloy strip of wide 8mm, long 1m.
The fusing point of the present embodiment 3 preparation-obtained middle layer alloy is 1063-1072 DEG C.Preparation-obtained for the present embodiment 3 middle layer alloy foil is applied to IC10 nickel base superalloy sample TLP welding among, welding condition is: welding temperature 1200 DEG C, soaking time 6h; Postwelding is warmed up to 1290 DEG C of insulation 4h; Then continue to be warming up to 1315 DEG C, and at this insulation 6h; Welding pressure 0.2-0.5MPa, vacuum tightness 5 × 10
-2pa.Heating schedule is: be heated to 1000 DEG C with the heat-up rate of 10 DEG C/min, insulation 30min; Welding temperature 1200 DEG C, after being incubated setting-up time, again heat up, be incubated and air cooling to room temperature, with reference to shown in Fig. 1.
The welding joint structure that the welding joint structure obtained and mother metal matching obtain well and mother metal match.
Embodiment 4
According to the step of above-described embodiment 1, the data according to embodiment in table 14 weigh each component element and content, and preparing thickness is 70 μm, the quick cooling alloy strip of wide 6mm, long 1.8m.
Preparation-obtained for the present embodiment 4 middle layer alloy foil is applied to the TLP welding of GH3039 nickel base superalloy sample, welding-heat treatment regime is: welding temperature 1200 DEG C, soaking time 5h; Postwelding is warmed up to 1290 DEG C of insulation 3h; Then continue to be warming up to 1315 DEG C, and at this insulation 7h; Welding pressure 0.2-0.5MPa, vacuum tightness 5 × 10
-2pa.Heating schedule is: be heated to 1000 DEG C with the heat-up rate of 10 DEG C/min, insulation 30min; Welding temperature 1200 DEG C, after being incubated setting-up time, again heat up, be incubated and air cooling to room temperature, with reference to shown in Fig. 1.
The welding joint structure obtained and mother metal match.
Embodiment 5
According to the step of above-described embodiment 1, the data according to embodiment in table 15 weigh the high pure metal of each component concentration, and preparing thickness is 80 μm, the quick cooling alloy strip of wide 7mm, long 1.4m.
Be applied in TLP method by preparation-obtained for the present embodiment 5 middle layer alloy foil, welding DD6 nickel-base high-temperature single crystal alloy sample, welding condition is: welding temperature 1200 DEG C, soaking time 6h; Postwelding is warmed up to 1290 DEG C of insulation 3h; Then continue to be warming up to 1315 DEG C, and at this insulation 8h; Welding pressure 0.2-0.5MPa, vacuum tightness 5 × 10
-2pa.Heating schedule is: be heated to 1000 DEG C with the heat-up rate of 10 DEG C/min, insulation 30min; Welding temperature 1200 DEG C, after being incubated setting-up time, again heat up, be incubated and air cooling to room temperature, with reference to shown in Fig. 1.
The welding joint structure obtained and mother metal match, and weld seam is single crystal organization.
In sum, middle layer of the present invention alloy, alloy foil snappiness is good, is convenient to processing and assembling; This middle layer alloy foil is applied to TLP and welds nickel base superalloy, good with the Organization Matching of nickel base superalloy; Apply this kind of middle layer alloy TLP and weld the welding-solution heat treatment of nickel base superalloy simply, production efficiency improves.Weldprocedure is stablized, and welding quality is easy to ensure, joint performance is promoted.
Claims (5)
1. the Nickel-base Alloy Interlayer for TLP weldering, its feature is: by atomic percent, composed of the following components: B is 3.2%-3.5%, Si be 2.4%-3%, Nd be 0.2%-0.4%, Co be 3%-4%, Cr be 1%-2%, W be 2.5%-3%, Ti be 1.2%-2%, Al be 1.5%-2.5%, Mo is 2%-3%, surplus is Ni, and total per-cent is 100%.
2. one kind uses the application method of Nickel-base Alloy Interlayer in TLP weldering-solution heat treatment described in claim 1, its feature is: first this middle layer fast chilling technique of Alloyapplication list roller is made as middle layer alloy foil, again middle layer alloy foil is placed between two nickel base superalloy samples to be welded, then according to TLP soldering method, the joint assembled heated, be incubated and slow cooling, thus realize the welding between nickel base superalloy.
3. application method according to claim 2, its feature is, in described TLP weldering process, welding-heat treatment process parameter is: welding temperature 1200 ± 5 DEG C, soaking time 4-6h; Postwelding is warmed up to 1290 ± 5 DEG C of insulation 3-5h; Then continue to be warming up to 1315 ± 5 DEG C, and at this insulation 6-8h; Welding pressure 0.2-0.5MPa, vacuum tightness 5 × 10
-2pa.
4. application method according to claim 3, its feature is, heating schedule is: be heated to 1000 DEG C with the heat-up rate of 10 DEG C/min, insulation 30min; Welding temperature 1200 ± 5 DEG C, after being incubated setting-up time, again heat up, be incubated and air cooling to room temperature.
5. application method according to claim 4, its feature is: actual temp control process is,
A section is the constant-speed heating stage, and heating rate is 10 DEG C/min;
B section is holding stage, namely at 1000 DEG C of insulation 30min;
C section is the constant-speed heating stage, and heating rate is 10 DEG C/min;
D section is isothermal holding stage, namely at 1200 DEG C of insulation 6h;
E section is the constant-speed heating stage, and heating rate is 10 DEG C/min;
F section is holding stage, namely at 1290 DEG C of insulation 3h;
G section is the constant-speed heating stage, and heating rate is 10 DEG C/min;
H section is holding stage, at 1315 DEG C of insulation 5h;
I section is the air cooling stage.
Priority Applications (1)
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| CN201410593770.1A CN104404307B (en) | 2014-10-29 | A kind of Nickel-base Alloy Interlayer and TLP thereof weld high temperature alloy technique |
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| CN201410593770.1A CN104404307B (en) | 2014-10-29 | A kind of Nickel-base Alloy Interlayer and TLP thereof weld high temperature alloy technique |
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| CN104404307A true CN104404307A (en) | 2015-03-11 |
| CN104404307B CN104404307B (en) | 2017-01-04 |
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Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN105200269A (en) * | 2015-11-09 | 2015-12-30 | 东方电气集团东方汽轮机有限公司 | Interlayer alloy as well as preparation method and application method thereof |
| CN105598543A (en) * | 2016-03-25 | 2016-05-25 | 中国科学院金属研究所 | Silicon-boron-containing interlayer alloy for bonding nickel-based high-temperature alloy or stainless steel and application thereof |
| CN108838578A (en) * | 2018-07-13 | 2018-11-20 | 广东省焊接技术研究所（广东省中乌研究院） | A kind of TLP diffusion welding (DW) powder intermediate layer and its welding method |
| CN109153095A (en) * | 2016-03-31 | 2019-01-04 | 泰克尼控股有限公司 | For forming the method and its connector of connector in binary system |
| CN110253175A (en) * | 2019-06-27 | 2019-09-20 | 西安理工大学 | Noncrystalline intermediate layer and Crystal Nickel-based Superalloy gradient TLP technique |
| CN111515517A (en) * | 2020-04-30 | 2020-08-11 | 中国航发哈尔滨东安发动机有限公司 | TLP (transient liquid phase) welding method for molybdenum-based superalloy |
| CN112008224B (en) * | 2020-10-19 | 2021-01-01 | 中国航发沈阳黎明航空发动机有限责任公司 | Connecting method of powder high-temperature alloy double-spoke-plate hollow turbine disc |
| CN116689932A (en) * | 2023-08-02 | 2023-09-05 | 杭州沈氏节能科技股份有限公司 | Diffusion welding method of micro-channel heat exchanger and welded product |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO1999021681A1 (en) * | 1997-10-27 | 1999-05-06 | Siemens Westinghouse Power Corporation | Method of bonding cast superalloys |
| CN102105260A (en) * | 2008-07-30 | 2011-06-22 | 三菱重工业株式会社 | Welding material for Ni-based alloy |
| CN102166687A (en) * | 2011-01-24 | 2011-08-31 | 河南理工大学 | Preparation method of heat-resisting steel tube instant liquid phase diffusion connection interlayer alloy |
| CN102251153A (en) * | 2011-07-06 | 2011-11-23 | 西安理工大学 | Interlayer alloy of DD6 nickel-based single crystal high temperature alloy used for transient liquid phase (TLP) bonding and preparation method thereof |
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO1999021681A1 (en) * | 1997-10-27 | 1999-05-06 | Siemens Westinghouse Power Corporation | Method of bonding cast superalloys |
| CN102105260A (en) * | 2008-07-30 | 2011-06-22 | 三菱重工业株式会社 | Welding material for Ni-based alloy |
| CN102166687A (en) * | 2011-01-24 | 2011-08-31 | 河南理工大学 | Preparation method of heat-resisting steel tube instant liquid phase diffusion connection interlayer alloy |
| CN102251153A (en) * | 2011-07-06 | 2011-11-23 | 西安理工大学 | Interlayer alloy of DD6 nickel-based single crystal high temperature alloy used for transient liquid phase (TLP) bonding and preparation method thereof |
Cited By (11)
| Publication number | Priority date | Publication date | Assignee | Title |
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| CN105200269A (en) * | 2015-11-09 | 2015-12-30 | 东方电气集团东方汽轮机有限公司 | Interlayer alloy as well as preparation method and application method thereof |
| CN105598543A (en) * | 2016-03-25 | 2016-05-25 | 中国科学院金属研究所 | Silicon-boron-containing interlayer alloy for bonding nickel-based high-temperature alloy or stainless steel and application thereof |
| CN105598543B (en) * | 2016-03-25 | 2018-01-02 | 中国科学院金属研究所 | A kind of connection of nickel base superalloy or stainless steel the intermediate layer alloy of siliceous boron and its application |
| CN109153095A (en) * | 2016-03-31 | 2019-01-04 | 泰克尼控股有限公司 | For forming the method and its connector of connector in binary system |
| US11141810B2 (en) | 2016-03-31 | 2021-10-12 | Techni Holding As | Non-eutectic bonding |
| CN108838578A (en) * | 2018-07-13 | 2018-11-20 | 广东省焊接技术研究所（广东省中乌研究院） | A kind of TLP diffusion welding (DW) powder intermediate layer and its welding method |
| CN110253175A (en) * | 2019-06-27 | 2019-09-20 | 西安理工大学 | Noncrystalline intermediate layer and Crystal Nickel-based Superalloy gradient TLP technique |
| CN111515517A (en) * | 2020-04-30 | 2020-08-11 | 中国航发哈尔滨东安发动机有限公司 | TLP (transient liquid phase) welding method for molybdenum-based superalloy |
| CN112008224B (en) * | 2020-10-19 | 2021-01-01 | 中国航发沈阳黎明航空发动机有限责任公司 | Connecting method of powder high-temperature alloy double-spoke-plate hollow turbine disc |
| CN116689932A (en) * | 2023-08-02 | 2023-09-05 | 杭州沈氏节能科技股份有限公司 | Diffusion welding method of micro-channel heat exchanger and welded product |
| CN116689932B (en) * | 2023-08-02 | 2023-10-31 | 杭州沈氏节能科技股份有限公司 | Diffusion welding method of micro-channel heat exchanger and welded product |
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