CN105385986A - Tungsten-based heavy alloy bar with gradient-changing hardness and producing method thereof - Google Patents
Tungsten-based heavy alloy bar with gradient-changing hardness and producing method thereof Download PDFInfo
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- CN105385986A CN105385986A CN201510760241.0A CN201510760241A CN105385986A CN 105385986 A CN105385986 A CN 105385986A CN 201510760241 A CN201510760241 A CN 201510760241A CN 105385986 A CN105385986 A CN 105385986A
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- alloy bar
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C10/00—Solid state diffusion of only metal elements or silicon into metallic material surfaces
- C23C10/28—Solid state diffusion of only metal elements or silicon into metallic material surfaces using solids, e.g. powders, pastes
- C23C10/34—Embedding in a powder mixture, i.e. pack cementation
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C27/00—Alloys based on rhenium or a refractory metal not mentioned in groups C22C14/00 or C22C16/00
- C22C27/04—Alloys based on tungsten or molybdenum
Abstract
The invention relates to a tungsten-based heavy alloy bar with the gradient-changing hardness and a producing method thereof and belongs to the technical field of powder metallurgy. Gradient distribution areas with the continuously-changing hardness are formed in the radial direction of the tungsten-based heavy alloy bar, and the area, with the largest hardness, in the gradient distribution areas with the continuously-changing hardness in the tungsten-based heavy alloy bar is the surface of the tungsten-based heavy alloy bar. The producing method of the tungsten-based heavy alloy bar includes the steps that a W-Ni-Fe alloy bar is used as a pack cementation object, a solid solution element is packed into the W-Ni-Fe alloy bar in a cementation manner through pack cementation treatment on the vacuum condition, and the tungsten-based heavy alloy bar with the gradient-changing hardness is obtained. The structural design of the bar is reasonable, the producing method is simple and controllable, and the performance of obtained finished products is excellent and stable. According to the tungsten-based heavy alloy bar and the producing method, industrial production and application are facilitated.
Description
Technical field
Tungsten Heavy Alloys rod that the present invention relates to the change of a kind of hardness gradient and preparation method thereof, belongs to powder metallurgical technology.
Background technology
Develop the developing direction that the heavy alloy with self-sharpening is armour piercing shot core material.Depleted uranium matrix material is the most excellent armour piercing shot core material of current Penetration Ability because having excellent self-sharpening.In the early 1990s in last century, based on depleted uranium material toxicity caused by world opinion and environmental protection pressure, the U.S. starts to develop alternative depleted uranium armor piercing shell core material.Researchist is on the basis of W-Ni-Fe system heavy alloy, by the change of alloy microstructure, as within the specific limits by increasing tungsten grain size, improve interfacial structure design, play the technical measures such as the intensity of the design of core geometric shape and strengthening Binder Phase and toughness and improve the Adiabatic Shearing Sensitivity of tungsten Heavy Alloys to improve its self-sharpening, though have made some progress, with Depleted Uranium Alloys also there is larger gap from sharpen effect.Meanwhile, by designing new tungstenalloy bullet core material system, as the W-Ni-Mn alloy of U.S.'s development, having close to sharpening performance with Depleted Uranium Alloys, is a kind of comparatively ideal armour piercing shot core material.But the tensile strength of the W-Ni-Mn alloy of preparation is usually at below 1000MPa, need to solve its low strength problem further.Beijing Institute of Technology, Central South University etc. also carried out the research that W-Ni-Mn alloy is prepared in liquid phase sintering, but because of alloy sintering densification degree not high enough, mechanical property is very low, is difficult to engineer applied.The research of the people such as K.J.Park finds, occurs that the noticeable change of tungsten particle size is easy to realize from sharpening in W-Ni-Fe heavy alloy.They devise a kind of composite structure tungstenalloy rod with tungsten grain size difference, namely utilize isostatic cool pressing technology to be embedded in by 97.4W (Mo)-1.1Ni-1.5Fe heavy alloy plug in 90W-7Ni-3Fe green compact overcoat and sinter composite structure into.Microstructure analysis result shows, and in core and outer tissue, refractory metal grain-size is respectively 30 μm, 46 μm.The Penetration Ability of the tungstenalloy of this composite structure improves 10% than traditional 93W-Ni-Fe heavy alloy, almost suitable with depleted uranium matrix material.But this technical matters is complicated, process control difficulties, there is the possibility of composite structure cracking in the huge contraction particularly occurred because of outer base substrate when liquid phase sintering, is difficult to realize through engineering approaches application.
At present, the main path improving the armour-piercing capability of traditional W-Ni-Fe system heavy alloy is swaged by sintered state alloy, implement deformation strengthening to improve the dynamic yield strength of tungsten Heavy Alloys, and then reach the object from sharp ability that namely its Adiabatic Shearing Sensitivity of raising strengthens tungstenalloy.But aximal deformation value causes the overall unit elongation (i.e. toughness) of tungsten Heavy Alloys bar sharply to reduce usually, increase penetrators and play risk in transmitting with disconnected during target.
Along with modern armor facing is strengthened day by day, the developing direction of armour piercing shot is the launching condition and the big L/D ratio bullet core material that adopt high gun pressure, high initial speed.In order to meet above-mentioned requirements, the tungsten Heavy Alloys bullet core material of high dynamic yield strength (high rigidity) and high tenacity must be developed.
Summary of the invention
In order to solve tungstenalloy from the contradiction between sharp ability and its toughness, the invention provides a kind of gradient-structure tungsten Heavy Alloys in alloy bar radial stiffness graded and manufacture method thereof, traditional W-Ni-Fe heavy alloy bar mechanical property radially (as hardness) is designed to gradient-structure, the i.e. core area of high tenacity and the outer region of high rigidity (high dynamic yield strength), with meet armour piercing shot core tungsten Heavy Alloys from sharp ability and high tenacity requirement.
The tungsten Heavy Alloys rod of a kind of hardness gradient change of the present invention, there is hardness continually varying gradient profile area along the radial direction of bar in described tungsten Heavy Alloys rod.
The tungsten Heavy Alloys rod of a kind of hardness gradient change of the present invention, the hardness on described tungsten Heavy Alloys rod surface is greater than the hardness of core.
The tungsten Heavy Alloys rod of a kind of hardness gradient change of the present invention, the region that in described tungsten Heavy Alloys rod, in hardness continually varying gradient profile area, hardness is maximum is described tungsten Heavy Alloys rod surface region.
The tungsten Heavy Alloys rod of a kind of hardness gradient of the present invention change, the thickness of described hardness continually varying gradient profile area in bar radial direction can regulate and control, and it depends primarily on the diameter of bar, bag oozes the factors such as time.General preferably 3-20mm.
The preparation method of the tungsten Heavy Alloys rod of a kind of hardness gradient change of the present invention, with W-Ni-Fe alloy bar for bag oozes object, under vacuum, process is oozed by bag, solution strengthening element bag is oozed in W-Ni-Fe alloy bar, obtains the tungsten Heavy Alloys rod of hardness gradient change; Described solid solution element energy solution strengthening W-Ni-Fe alloy bar, and solid solution element does not react with any one or multiple element in W-Ni-Fe alloy bar and generates fragility mesophase spherule.
The preparation method of the tungsten Heavy Alloys rod of a kind of hardness gradient change of the present invention, with W-Ni-Fe alloy bar for bag oozes object, W-Ni-Fe alloy bar is embedded in the mixed powder be made up of solid solution element simple substance and/or powdered alloy and inertia oxide powder, be less than or equal to the condition of 5Pa in Absolute truth reciprocal of duty cycle under; Carry out bag in 1300-1400 DEG C and ooze process, solid solution element bag is oozed in W-Ni-Fe alloy bar, obtain the tungsten Heavy Alloys rod of hardness gradient change; Described solid solution element energy solution strengthening W-Ni-Fe alloy bar, and solid solution element does not react with any one or multiple element in W-Ni-Fe alloy bar and generates fragility mesophase spherule.
Because tungsten Heavy Alloys sinters usually in hydrogeneous atmosphere, usually cause hydrogen embrittlement.As for generally all needing during armour piercing shot core material, vacuum dehydrogenation process is carried out to tungsten Heavy Alloys rod.In order to reduce manufacturing cost and simplified manufacturing technique, when the bag of alloy bar oozes process, need strict its vacuum tightness of control.
The preparation method of the tungsten Heavy Alloys rod of a kind of hardness gradient change of the present invention, described W-Ni-Fe alloy bar, comprises with atomic percentage:
W90-95%, is preferably 92%
Ni1-7%, is preferably 5.6%;
Fe0.5-3%, is preferably 2.4%.
The preparation method of the tungsten Heavy Alloys rod of a kind of hardness gradient change of the present invention, is also applicable to other section bar of other tungsten-bast alloy bars or tungsten base.
The preparation method of the tungsten Heavy Alloys rod of a kind of hardness gradient change of the present invention, described solid solution element is selected from least one in Mo, Cr, Ti.
The preparation method of the tungsten Heavy Alloys rod of a kind of hardness gradient change of the present invention, described W-Ni-Fe alloy bar is the W-Ni-Fe alloy bar of sintered state.
The preparation method of the tungsten Heavy Alloys rod of a kind of hardness gradient change of the present invention, the granularity of described solid solution element simple substance and/or powdered alloy is 2-30 micron.
The preparation method of the tungsten Heavy Alloys rod of a kind of hardness gradient change of the present invention, in affiliated mixed powder, solid solution element simple substance and/or powdered alloy account for the 50%-55% of mixed powder cumulative volume.
The preparation method of the tungsten Heavy Alloys rod of a kind of hardness gradient of the present invention change, described inertia oxide powder is the aluminium sesquioxide powder crossed of more than 1400 DEG C temperature calcination and/or Zirconium oxide powder.
The preparation method of the tungsten Heavy Alloys rod of a kind of hardness gradient change of the present invention, the time that bag oozes process is wrapped the alloy bar diameter and temperature that ooze and is determined, and generally can obtain the gradient-structure tungsten Heavy Alloys bar that hardness changes in gradient after the bag of 1.5-3 hour oozes process.
Principle and advantage
The present invention devises the tungsten Heavy Alloys rod of hardness along radially Gradient distribution; By the synergy of each preparation parameter and project organization, the contradiction between strong, the Hardness and toughness efficiently solving tungsten Heavy Alloys.
The present invention achieves hardness radially Gradient distribution in tungsten Heavy Alloys rod, the particularly poor alloying element of its core area, namely obtain the tungsten Heavy Alloys rod core area of high tenacity, and outer region realizes hardening by the solution strengthening of alloying element to Binder Phase and tungsten grain.By the rational Match on the core of tungsten Heavy Alloys rod, hardness continually varying gradient profile area, surface, provide prerequisite for obtaining having high dynamic yield strength (high rigidity) concurrently with the tungsten Heavy Alloys bullet core of high tenacity.
Embodiment
Embodiment 1: bag oozes the preparation of molybdenum gradient-structure tungsten Heavy Alloys rod
First the molybdenum powder of 2.5 microns of 50% (volume fraction) is mixed 3 hours with the alumina powder ball milling calcined.Be that the sintered state 92W-5.6Ni-2.4Fe alloy bar of 12mm is imbedded in the molybdenum boat or corundum boat filling Mo powder+aluminum oxide powder by diameter, load and do in the vacuum oven of heating element with molybdenum sheet or leaf.Extract furnace air out to below 5Pa, be warming up to 1350 DEG C by the speed of 10 DEG C/min, be incubated 2 hours, cool to room temperature with the furnace.From alloy bar surface to 2.5mm under upper layer, alloy bar microhardness is reduced to 220HV continuously from 380HV.
Embodiment 2: bag oozes the preparation of the gradient-structure tungsten Heavy Alloys rod of Ti
First the titanium valve of 25 microns of 50% (volume fraction) is mixed 3 hours with the alumina powder ball milling calcined.Be that the sintered state 92W-5.6Ni-2.4Fe alloy bar of 12mm is imbedded in the molybdenum boat or corundum boat filling Ti powder+aluminum oxide powder by diameter, load and do in the vacuum oven of heating element with molybdenum sheet or leaf.Extract furnace air out to below 5Pa, be warming up to 1300 DEG C by the speed of 10 DEG C/min, be incubated 2 hours, cool to room temperature with the furnace.From alloy bar surface to 2.5mm under upper layer, alloy bar microhardness is reduced to 320HV continuously from 395HV.
Embodiment 3: bag oozes the preparation of the gradient-structure tungsten Heavy Alloys of Cr
First the Cr powder of 16 microns of 50% (volume fraction) is mixed 3 hours with the alumina powder ball milling calcined.Be that the sintered state 92W-5.6Ni-2.4Fe alloy bar of 12mm is imbedded in the molybdenum boat or corundum boat filling Cr powder+aluminum oxide powder by diameter, load and do in the vacuum oven of heating element with molybdenum sheet or leaf.Extract furnace air out to below 5Pa, be warming up to 1300 DEG C by the speed of 10 DEG C/min, be incubated 2 hours, cool to room temperature with the furnace.From alloy bar surface to 2.5mm under upper layer, alloy bar microhardness is reduced to 335HV continuously from 373HV.
Claims (10)
1. the tungsten Heavy Alloys rod of a hardness gradient change, is characterized in that: described tungsten Heavy Alloys rod exists hardness continually varying gradient profile area along the radial direction of bar.
2. the tungsten Heavy Alloys rod of a kind of hardness gradient change according to claim 1, is characterized in that: the hardness on described tungsten Heavy Alloys rod surface is greater than the hardness of core.
3. the tungsten Heavy Alloys rod of a kind of hardness gradient change according to claim 1, is characterized in that: the region that in described tungsten Heavy Alloys rod, in hardness continually varying gradient profile area, hardness is maximum is described tungsten Heavy Alloys rod surface.
4. the preparation method of the tungsten Heavy Alloys rod of a kind of hardness gradient change as described in claim 1-3 any one, it is characterized in that: with W-Ni-Fe alloy bar for bag oozes object, under vacuum, process is oozed by bag, solid solution element bag is oozed in W-Ni-Fe alloy bar, obtains the tungsten Heavy Alloys rod of hardness gradient change; Described solid solution element energy solution strengthening W-Ni-Fe alloy bar, and solid solution element does not react with any one or multiple element in W-Ni-Fe alloy bar and generates fragility mesophase spherule.
5. a kind of preparation method preparing the tungsten Heavy Alloys rod of hardness gradient change according to claim 4, it is characterized in that: with W-Ni-Fe alloy bar for bag oozes object, W-Ni-Fe alloy bar is embedded in the mixed powder be made up of solid solution element simple substance and/or powdered alloy and inertia oxide powder, be less than or equal to the condition of 5Pa in Absolute truth reciprocal of duty cycle under; Carry out bag in 1300-1400 DEG C and ooze process, solid solution element bag is oozed in W-Ni-Fe alloy bar, obtain the tungsten Heavy Alloys rod of hardness gradient change; Described solid solution element energy solution strengthening W-Ni-Fe alloy bar, and solid solution element does not react with any one or multiple element in W-Ni-Fe alloy bar and generates fragility mesophase spherule.
6. a kind of preparation method preparing the tungsten Heavy Alloys rod of hardness gradient change according to claim 4 or 5, is characterized in that: described W-Ni-Fe alloy bar, comprises with atomic percentage:
W90-95％；
Ni1-7％；
Fe0.5-3％。
7. a kind of preparation method preparing the tungsten Heavy Alloys rod of hardness gradient change according to claim 4 or 5, is characterized in that: described solid solution element is selected from least one in Mo, Cr, Ti.
8. a kind of preparation method preparing the tungsten Heavy Alloys rod of hardness gradient change according to claim 4 or 5, is characterized in that: described W-Ni-Fe alloy bar is the W-Ni-Fe alloy bar of sintered state.
9. a kind of preparation method preparing the tungsten Heavy Alloys rod of hardness gradient change according to claim 5, is characterized in that: the granularity of described solid solution element simple substance and/or powdered alloy is 2-30 micron.
10. a kind of preparation method preparing the tungsten Heavy Alloys rod of hardness gradient change according to claim 5, is characterized in that:
In described mixed powder, solid solution element simple substance and/or powdered alloy account for the 50%-55% of mixed powder cumulative volume;
Described inertia oxide powder is the aluminium sesquioxide powder crossed of more than 1400 DEG C temperature calcination and/or Zirconium oxide powder.
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Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN105861980A (en) * | 2016-05-25 | 2016-08-17 | 广州新莱福磁电有限公司 | Anti-corrosion method for high-gravity alloy |
| CN106521279A (en) * | 2016-12-05 | 2017-03-22 | 郑州丽福爱生物技术有限公司 | High-strength alloy material and preparation method thereof |
| CN107937782A (en) * | 2017-11-23 | 2018-04-20 | 湖北工业大学 | A kind of preparation method of gradient Mg Zn alloy bars |
| CN107956942A (en) * | 2017-10-27 | 2018-04-24 | 宁波天鑫金属软管有限公司 | A kind of mechanical sleeves and preparation method thereof |
| CN108642439A (en) * | 2018-06-05 | 2018-10-12 | 合肥工业大学 | A method of preparing high-strength coating in tungsten alitizing |
| WO2021027824A1 (en) * | 2019-08-12 | 2021-02-18 | 河南科技大学 | Tungsten-base alloy material and preparation method therefor |
| CN114293082A (en) * | 2021-12-28 | 2022-04-08 | 海特信科新材料科技有限公司 | Tungsten-based alloy for nuclear medical shielding and preparation method thereof |
| CN114480935A (en) * | 2022-01-20 | 2022-05-13 | 广东工业大学 | Tungsten-based alloy with grain size having gradient effect and preparation method thereof |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101333640A (en) * | 2007-06-29 | 2008-12-31 | 福田金属箔粉工业株式会社 | Powder for infiltration |
-
2015
- 2015-11-10 CN CN201510760241.0A patent/CN105385986B/en not_active Expired - Fee Related
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101333640A (en) * | 2007-06-29 | 2008-12-31 | 福田金属箔粉工业株式会社 | Powder for infiltration |
Non-Patent Citations (3)
| Title |
|---|
| 中国机械工程学会等: "《中国材料工程大典》", 31 January 2006, 化学工业出版社 * |
| 金莹: "梯度结构钨基重合金制备及性能的研究", 《中国优秀硕士学位论文全文数据库 工程科技I辑》 * |
| 黄劲松等: "钨基重合金的烧结", 《粉末冶金工业》 * |
Cited By (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN105861980A (en) * | 2016-05-25 | 2016-08-17 | 广州新莱福磁电有限公司 | Anti-corrosion method for high-gravity alloy |
| CN106521279A (en) * | 2016-12-05 | 2017-03-22 | 郑州丽福爱生物技术有限公司 | High-strength alloy material and preparation method thereof |
| CN107956942A (en) * | 2017-10-27 | 2018-04-24 | 宁波天鑫金属软管有限公司 | A kind of mechanical sleeves and preparation method thereof |
| CN107956942B (en) * | 2017-10-27 | 2023-08-22 | 宁波天鑫金属软管有限公司 | Mechanical sleeve and preparation method thereof |
| CN107937782A (en) * | 2017-11-23 | 2018-04-20 | 湖北工业大学 | A kind of preparation method of gradient Mg Zn alloy bars |
| CN107937782B (en) * | 2017-11-23 | 2019-06-11 | 湖北工业大学 | A kind of preparation method of gradient Mg-Zn alloy bar |
| CN108642439A (en) * | 2018-06-05 | 2018-10-12 | 合肥工业大学 | A method of preparing high-strength coating in tungsten alitizing |
| CN108642439B (en) * | 2018-06-05 | 2020-04-14 | 合肥工业大学 | Method for preparing high-strength coating on surface of metal tungsten through aluminizing |
| WO2021027824A1 (en) * | 2019-08-12 | 2021-02-18 | 河南科技大学 | Tungsten-base alloy material and preparation method therefor |
| CN114293082A (en) * | 2021-12-28 | 2022-04-08 | 海特信科新材料科技有限公司 | Tungsten-based alloy for nuclear medical shielding and preparation method thereof |
| CN114480935A (en) * | 2022-01-20 | 2022-05-13 | 广东工业大学 | Tungsten-based alloy with grain size having gradient effect and preparation method thereof |
| CN114480935B (en) * | 2022-01-20 | 2022-11-29 | 广东工业大学 | Tungsten-based alloy with grain size having gradient effect and preparation method thereof |
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