CN103540803A - High hardness non-magnetic nichrome and preparation method thereof - Google Patents
High hardness non-magnetic nichrome and preparation method thereof Download PDFInfo
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Abstract
The invention relates to a high hardness non-magnetic nichrome and a preparation method thereof. The nichrome comprises the following components in percentage by weight: 37-38% of Cr, 3.3-3.5% of Al, 1.6-2.3% of W, 0.005-0.03% of Y, no more than 0.015% of C, no more than 0.010% of S, no more than 0.010% of P, no more than 0.10% of Si, no more than 0.015% of Mn and the balance of Ni; and the nichrome is prepared by the steps of smelting, homogenizing, cogging and hot rolling, solution treating, cold drawing and aging. The nichrome is obtained by appropriately adding the contents of W and Y elements and reducing the content of Cr on the basis of the components of a common high hardness non-magnetic nichrome, the hardness of the nichrome is increased through combining the cold deformation with the aging temperature of the nichrome, various factors are fully taken into consideration, and finally, the high hardness non-magnetic nichrome with excellent performance is obtained.
Description
Technical field
The present invention relates to a kind of nickel-base alloy, particularly a kind of have a non-magnetic nichrome of high rigidity.
Background technology
Alloy of the present invention belongs to the high elastic modulus alloy in the elastic alloy category in Precise Alloy field.This alloy can, for precision optical machinery fields such as instrument, as pivot, pull spring, hairspring, clockwork spring, spring, diaphragm and bearing, ball, press tool, cutter etc., have a wide range of applications background.
High rigidity comprises Co base and Ni base alloy without magnetic high elastic modulus alloy, and the product grade forming at present mainly contains: 3J21(Co40Cr20Ni16Fe15Mo7), 3J22(Co40Cr20Ni16Fe15Mo4W4), 3J23(Co40Cr20Ni16Fe15Mo4W4Ce), 3YC11(Co42Ni25Cr18Mo4W10Ce), 3YC15(Co26Ni16Cr40W17AlCe) etc. Co base alloy and 3J40(Ni55Cr40Al3.5Ce) Ni base alloy.3J21,3J22,3J23,3YC11,3YC15 belong to working hardening type Co base alloy, must through timeliness, just can show good elasticity performance again by very large cold deformation later, its HRc hardness is all below 65, and its χ v volume susceptibility is all more than 400 * 10-6.3J40 belongs to precipitation strength type alloy, under solid solution condition, there is good plasticity, after ageing treatment, can obtain strengthening significantly, simple timeliness thermal treatment can make the HRc hardness of 3J40 improve more than 20, solid solution+timeliness of 3J40 and cold deformation+aged, its HRc hardness value best result Bie Keda 59 and 64, its χ v volume susceptibility is all more than 40 * 10-6.Above high-intensity non-magnetic high elastic modulus alloy, through the development of more than 30 years, relies on its good over-all properties, obtains a wide range of applications at present.Along with scientific and technological development, in some special industry, such high-intensity non-magnetic elastic alloy is had higher requirement to meet current service requirements.
Summary of the invention
The object of the invention is to propose a kind of nichrome material with the low magnetic of high rigidity, design and optimization by alloy composition complete.
Another object of the present invention has been to provide the preparation method of above-mentioned alloy, by adjusting the preparation technology of this composition alloy, realizes high rigidity and non-magnetic object.
For achieving the above object, the invention provides following technical scheme:
Without a magnetic nichrome, the composition of this alloy is by weight percentage: Cr:37～38, and Al:3.3～3.5, W:1.6～2.3, Y:0.005～0.03, C≤0.015, S≤0.010, P≤0.010, Si≤0.10, Mn≤0.015, all the other are Ni;
This alloy is prepared by smelting, homogenizing processing, cogging and hot rolling, solution treatment, cold drawn and ageing treatment step.
This alloy in the metallographic structure of the state of use is: the austenitic matrix that crystal grain is tiny and the γ ' strengthening phase Ni separating out
3the WC of Al, α-Cr phase and trace.
Solution treatment process obtains the single-phase austenite structure that crystal grain is tiny.
In described solution treatment process, separate out globular α-Cr phase, in ageing treatment process, the Ni of Al and matrix produces γ ' strengthening precipitated phase Ni
3al.
A preparation method for the non-magnetic nichrome of high rigidity, comprises the steps:
1) batching melting, the composition of this alloy is by weight percentage: Cr:37～38, Al:3.3～3.5, W:1.6～2.3, Y:0.005～0.03, C≤0.015, S≤0.010, P≤0.010, Si≤0.10, Mn≤0.015, all the other are Ni; Adopt vacuum induction and the vacuum melting of vacuum consumable duplex, vacuum tightness≤1 * 10-1Pa;
2) homogenizing annealing is processed: alloy pig is placed in to High Temperature Furnaces Heating Apparatus and at 1100-1200 ℃, is incubated 0.5-2 hour;
3) cogging, heat are pricked: while stripping off the skin ingot cogging, lower than 600 ℃ of shove charges, through 1190～1210 ℃ of insulations, after 0.5-1 hour, be forged into square billet, then after 1190～1210 ℃ of insulation 0.5-1, be rolled into dish circle;
4) solution treatment: be incubated 20～60 minutes at 1180～1200 ℃, hardening, obtains the tiny single-phase austenite structure of crystal grain rapidly;
5) cold drawn: dish circle obtains the surperficial no marking product of desired size through cold deformation;
6) ageing treatment: the bar after cold drawn is incubated 4-5 hour at 500-625 ℃.
Described solution treatment process obtains the single-phase austenite structure that crystal grain is tiny.
In described solution treatment process, separate out globular α-Cr phase, in ageing treatment process, the Ni of Al and matrix produces γ ' strengthening precipitated phase Ni
3al.
The deflection of described cold drawn step is 75%-90%.
Based on above-mentioned purpose, we adopt Ni-38Cr-3Al-W on the Composition Design of alloy is main component.This alloy be take Ni, Cr as basal component, and appropriate Al can separate out with the Ni of matrix face-centered cubic γ ' strengthening phase (Ni in timeliness thermal treatment
3al), in solution treatment process, separate out globular α-Cr phase, the appropriate W solid solution of adding is in matrix and separate out micro-WC, these combined factors get up to put forward heavy alloyed hardness, the processing characteristics of Cr, W, Al content and alloy is in close relations, along with increasing of constituent content in alloy, the fragility of alloy obviously strengthens, and is unfavorable for the processed and applied of alloy; Along with the reduction of alloying element content, the plasticity of alloy obviously strengthens, and is beneficial to the processed and applied of alloy, but intensity and hardness obviously reduce.The variation of Al content will affect the solid solubility temperature of alloy, and content increases, and will carry heavy alloyed solid solubility temperature, and Al participates in Precipitation behavior in ag(e)ing process, and therefore the appropriate Al that contains measures particularly crucial.W participates in Precipitation behavior as solution strengthening element simultaneously, increases intensity and the hardness of alloy, and low-alloyed processing characteristics, falls in W too high levels.Y purifies element as alloy, can effectively reduce the content of the impurity element of alloy.The present invention, according to the effect of each element in alloy, needs rational allocation, suitably reduces Cr content during design alloying constituent, and the appropriate alloying elements such as W, Y that add make alloy have unique over-all properties simultaneously.The composition of alloy of the present invention should be controlled at (% by weight) Cr:37～38, Al:3.3～3.5, and W:1.6～2.3, Y:0.005～0.0.03, C≤0.015, S≤0.010, P≤0.010, Si≤0.10, Mn≤0.015, all the other are Ni.
Obtain and there is the NiCr alloy that the high magnetic of hardness is low, except alloying constituent, guarantee that alloy property also needs to adopt the preparation method of the alloys such as suitable complete processing and thermal treatment process.
Prepare as follows the non-magnetic nichrome of high rigidity of the present invention:
1, melting
Before molten alloy, the surface oxide layer of metal Ni to be removed through polishing.Alloy melting will pass through vacuum induction and vacuum consumable duplex vacuum, and vacuum tightness≤1 * 10-1Pa will strictly control the scaling loss amount of alloying element in fusion process.
2, homogenizing is processed
Alloy pig is placed in to High Temperature Furnaces Heating Apparatus and carries out long-time homogenizing annealing processing, the also chemical composition of sampling analysis alloy strips off the skin after processing.
3, cogging, heat are pricked
While stripping off the skin ingot cogging, lower than 600 ℃ of shove charges, the size of alloy pig determines the heat-up rate speed of alloy pig, after 1190～1210 ℃ of insulation appropriate times, starts to be forged into square billet.After 1190～1210 ℃ of insulation appropriate times, be rolled into dish circle again.
4, solution heat treatment
Dish circle solution heat treatment temperature is 1180～1200 ℃, is incubated 20～60 minutes, and hardening, obtains the tiny single-phase austenite structure of crystal grain rapidly.Guaranteeing, under the condition of complete solid solution, should to select lower solid solubility temperature as far as possible.
5, cold drawn
Light bar is cold drawn to desired size by different cold deformations.Attentional selection lubricant and pass deformation in cold drawing process, accomplish surperficial no marking.
6, ageing treatment: the bar after cold drawn, after being processed into required part, being incubated 4-5 hour and carrying out timeliness thermal treatment at 500-625 ℃.
The NiCr alloy the present invention relates to, on the basis of common nonmagnetic high-hardness alloy (domestic trade mark 3J40) composition, suitably add the content of W and Y element, reduce Cr, put forward heavy alloyed hardness, the hardness that regulates alloy that coordinates by alloy cold deformation with aging temp, the NiCr alloy the present invention relates to has fully taken into account the effect of various factors, has finally prepared the nonmagnetic NiCr alloy of high rigidity of excellent property.
Accompanying drawing explanation
Fig. 1 is in embodiments of the invention, and solid solution state alloy bar material is carried out to cold drawn rear 550 ℃, 575 ℃, 600 ℃, 625 ℃ * 5h ageing treatment, the hardness of the alloy after the solid solution+timeliness of gained of carrying out respectively;
Fig. 2 is the susceptibility of embodiment alloy in Fig. 1;
Fig. 3 be in Fig. 1 embodiment alloy through the hardness of the sample of cold drawn tube reducing and 500 ℃ of ageing treatment;
Fig. 4 is the susceptibility of embodiment alloy in Fig. 3.
Embodiment
Below in conjunction with embodiment, the present invention is described in detail.
1, with the vacuum consumable electrode ingot (being of a size of Φ 80mm) of 2 of 25Kg vacuum induction meltings (1#, 2#) composition, consumable ingot is prepared the vacuum consumable electrode of 2 compositions after car light tack, and the high rigidity after vacuum consumable is as shown in table 1 without magnetic NiCr alloy steel ingot and the contrast of ripe trade mark product composition:
Table 1 alloying constituent
2, alloy pig is processed through 1 hour homogenizing annealing in 1200 ℃, in 1180 ℃ of insulations, within 1 hour, be forged into square billet, square billet is rolled into Φ 10mm dish circle through 1180 ℃ of insulations after 1 hour, dish circle is hardening after 1200 ℃ of insulation 20min solution treatment, obtain solid solution condition alloy disc circle, dish circle obtains Φ 9.5mm vertical bar NiCr alloy bar material after straight polishing.
3, solid solution state alloy bar material is carried out to cold drawn rear carry out respectively 550 ℃, 575 ℃, 600 ℃, 625 ℃ * 5h ageing treatment, the alloy after the solid solution+timeliness of gained has performance as shown in Figure 1, 2.
4, by Φ 9.5mm solid solution condition alloy through cold drawn tube reducing, attentional selection lubricant and pass deformation in cold drawing process, accomplish surperficial no marking.Then the sample that carries out 500 ℃ of ageing treatment has performance as shown in Figure 3,4.
By optimized alloy element, coordinate suitable preparation technology, prepared there is premium properties high rigidity without magnetic nichrome.The hardness HRc > 60.5 of the solid solution aging state of development alloy, reaches as high as 62, and the hardness HRc > 65 of cold deformation aged, reaches as high as 67.5, and volume susceptibility < 28 * 10
-6.
Claims (8)
1. high rigidity, without a magnetic nichrome, is characterized in that, the composition of this alloy is by weight percentage: Cr:37～38, Al:3.3～3.5, W:1.6～2.3, Y:0.005～0.03, C≤0.015, S≤0.010, P≤0.010, Si≤0.10, Mn≤0.015, all the other are Ni;
This alloy is prepared by smelting, homogenizing processing, cogging and hot rolling, solution treatment, cold drawn and ageing treatment step.
2. high rigidity according to claim 1, without magnetic nichrome, is characterized in that, described this alloy in the metallographic structure of the state of use is: the austenitic matrix that crystal grain is tiny and the γ ' strengthening phase Ni separating out
3the WC of Al, α-Cr phase and trace.
3. high rigidity according to claim 2, without magnetic nichrome, is characterized in that, described solution treatment obtains the single-phase austenite structure that crystal grain is tiny.
4. high rigidity according to claim 1, without magnetic nichrome, is characterized in that, separates out globular α-Cr phase in described solution treatment process, and in ageing treatment process, the Ni of Al and matrix produces γ ' strengthening precipitated phase Ni
3al.
5. the preparation method of the non-magnetic nichrome of high rigidity as claimed in claim 1, is characterized in that, comprises the steps:
1) batching melting, the composition of this alloy is by weight percentage: Cr:37～38, Al:3.3～3.5, W:1.6～2.3, Y:0.005～0.03, C≤0.015, S≤0.010, P≤0.010, Si≤0.10, Mn≤0.015, all the other are Ni; Adopt vacuum induction and the vacuum melting of vacuum consumable duplex, vacuum tightness≤1 * 10-1Pa;
2) homogenizing annealing is processed: alloy pig is placed in to High Temperature Furnaces Heating Apparatus and at 1100-1200 ℃, is incubated 0.5-2 hour;
3) cogging, heat are pricked: while stripping off the skin ingot cogging, lower than 600 ℃ of shove charges, through 1190～1210 ℃ of insulations, after 0.5-1 hour, be forged into square billet, then after 1190～1210 ℃ of insulation 0.5-1, be rolled into dish circle;
4) solution treatment: be incubated 20～60 minutes at 1180～1200 ℃, hardening, obtains the tiny single-phase austenite structure of crystal grain rapidly;
5) cold drawn: dish circle obtains the surperficial no marking product of desired size through cold deformation;
6) ageing treatment: the bar after cold drawn is incubated 4-5 hour at 500-625 ℃.
6. preparation method according to claim 5, is characterized in that, described solution treatment obtains the single-phase austenite structure that crystal grain is tiny.
7. preparation method according to claim 5, is characterized in that, separates out globular α-Cr phase in described solution treatment process, and in ageing treatment process, the Ni of Al and matrix produces γ ' strengthening precipitated phase Ni
3al.
8. preparation method according to claim 5, is characterized in that, the deflection of described cold drawn step is 75%-90%.
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Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104178648A (en) * | 2014-09-12 | 2014-12-03 | 重庆材料研究院有限公司 | Preparation method of nonmagnetic corrosion-resistant nickel-chromium-base bearing alloy |
| CN104233137A (en) * | 2014-08-26 | 2014-12-24 | 盐城市鑫洋电热材料有限公司 | Deformation and thermal treatment technology of nichrome alloy |
| CN105925849A (en) * | 2016-05-04 | 2016-09-07 | 中国第重型机械股份公司 | Control method for nickel-based alloy forgings for 700-DEG C ultra-supercritical steam turbine rotor |
| CN107794410A (en) * | 2017-10-27 | 2018-03-13 | 桂林市漓江机电制造有限公司 | A kind of high tenacity nichrome |
| CN108546834A (en) * | 2018-04-16 | 2018-09-18 | 北京科技大学 | A kind of nickel base superalloy master alloy sublimate method of smelting |
| CN110136902A (en) * | 2019-05-08 | 2019-08-16 | 凌海科诚电气股份公司 | A kind of high voltage non-inductance resistor device and preparation method thereof |
| CN113684434A (en) * | 2021-07-29 | 2021-11-23 | 宝钛集团有限公司 | Preparation method of Inconel nickel-chromium alloy wide medium plate |
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Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104233137A (en) * | 2014-08-26 | 2014-12-24 | 盐城市鑫洋电热材料有限公司 | Deformation and thermal treatment technology of nichrome alloy |
| CN104178648A (en) * | 2014-09-12 | 2014-12-03 | 重庆材料研究院有限公司 | Preparation method of nonmagnetic corrosion-resistant nickel-chromium-base bearing alloy |
| CN104178648B (en) * | 2014-09-12 | 2016-08-03 | 重庆材料研究院有限公司 | The preparation method of the chromio bearing metal of ni-resist without magnetic |
| CN105925849A (en) * | 2016-05-04 | 2016-09-07 | 中国第重型机械股份公司 | Control method for nickel-based alloy forgings for 700-DEG C ultra-supercritical steam turbine rotor |
| CN107794410A (en) * | 2017-10-27 | 2018-03-13 | 桂林市漓江机电制造有限公司 | A kind of high tenacity nichrome |
| CN108546834A (en) * | 2018-04-16 | 2018-09-18 | 北京科技大学 | A kind of nickel base superalloy master alloy sublimate method of smelting |
| CN110136902A (en) * | 2019-05-08 | 2019-08-16 | 凌海科诚电气股份公司 | A kind of high voltage non-inductance resistor device and preparation method thereof |
| CN113684434A (en) * | 2021-07-29 | 2021-11-23 | 宝钛集团有限公司 | Preparation method of Inconel nickel-chromium alloy wide medium plate |
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