CN103540803B - A kind of high rigidity is without magnetic nichrome and preparation method thereof - Google Patents
A kind of high rigidity is without magnetic nichrome and preparation method thereof Download PDFInfo
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- CN103540803B CN103540803B CN201310525021.0A CN201310525021A CN103540803B CN 103540803 B CN103540803 B CN 103540803B CN 201310525021 A CN201310525021 A CN 201310525021A CN 103540803 B CN103540803 B CN 103540803B
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Abstract
The present invention relates to a kind of high rigidity without magnetic nichrome and preparation method thereof, 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 smeltings, Homogenization Treatments, cogging and hot rolling, solution treatment, cold drawn and ageing treatment step.Nichrome of the present invention, on the basis of common nonmagnetic high-hardness alloy composition, content, the reduction Cr of suitable interpolation W and Y element obtain, the hardness that improve alloy is coordinated by alloy cold deformation and aging temp, and fully take into account the effect of various factors, finally obtain the nonmagnetic nichrome of high rigidity of excellent property.
Description
Technical field
The present invention relates to a kind of nickel-base alloy, particularly one has the 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 may be used for the precision optical machinery fields such as instrument, as pivot, pull spring, hairspring, clockwork spring, spring, diaphragm and bearing, ball, press tool, cutter etc., has 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 formed at present mainly contains: Co base alloy and 3J40 (Ni55Cr40Al3.5Ce) the Ni base alloys such as 3J21 (Co40Cr20Ni16Fe15Mo7), 3J22 (Co40Cr20Ni16Fe15Mo4W4), 3J23 (Co40Cr20Ni16Fe15Mo4W4Ce), 3YC11 (Co42Ni25Cr18Mo4W10Ce), 3YC15 (Co26Ni16Cr40W17AlCe).3J21,3J22,3J23,3YC11,3YC15 belong to working hardening type Co base alloy, just must can show good elasticity performance through timeliness again by very large cold deformation later, its HRc hardness is all below 65, and its χ v volume susceptibility is all at 400 × more than 10-6.3J40 belongs to precipitation strength type alloy, under solid solution condition, there is good plasticity, can obtain after ageing treatment and strengthen significantly, simple aging strengthening model can make the HRc hardness of 3J40 improve more than 20, solid solution+the 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 at 40 × more than 10-6.Above high-intensity non-magnetic high elastic modulus alloy, through the development of more than 30 years, by means of the over-all properties that it is good, obtains a wide range of applications at present.Along with the development of science and technology, in some special industry, have higher requirement to meet current service requirements to such high-intensity non-magnetic elastic alloy.
Summary of the invention
The object of the invention is to propose a kind of nichrome material with the low magnetic of high rigidity, completed by the design of alloy composition and optimization.
Another object of the present invention there is provided the preparation method of above-mentioned alloy, realizes high rigidity and non-magnetic object by the preparation technology adjusting this composition alloy.
For achieving the above object, the invention provides following technical scheme:
A kind of high rigidity is without magnetic nichrome, and 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, and all the other are Ni;
This alloy is prepared by smeltings, Homogenization Treatments, cogging and hot rolling, solution treatment, cold drawn and ageing treatment step.
This alloy in using state metallographic structure is: the γ ' strengthening phase Ni of the austenitic matrix that crystal grain is tiny and precipitation
3the WC of Al, α-Cr phase and trace.
Solution treatment process obtains the tiny single phase austenite tissue of crystal grain.
Separate out globular α-Cr phase in described solution treatment process, in ageing 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 also 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, and all the other are Ni; Adopt vacuum induction and the vacuum melting of vacuum consumable duplex, vacuum tightness≤1 × 10
-1pa;
2) homogenizing annealing process: alloy pig is placed in High Temperature Furnaces Heating Apparatus and is incubated 0.5-2 hour at 1100-1200 DEG C;
3) cogging, heat prick: strip off the skin ingot cogging time lower than 600 DEG C of shove charges, through 1190 ~ 1210 DEG C insulation 0.5-1 hour after be forged into square billet, then 1190 ~ 1210 DEG C insulation 0.5-1 hour after be rolled into dish circle;
4) solution treatment: be incubated 20 ~ 60 minutes at 1180 ~ 1200 DEG C, rapid hardening, obtains the single phase austenite tissue that crystal grain is tiny;
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 DEG C.
Described solution treatment process obtains the tiny single phase austenite tissue of crystal grain.
Separate out globular α-Cr phase in described solution treatment process, in ageing process, the Ni of Al and matrix produces γ ' strengthening precipitated phase Ni
3al.
The deflection of described cold drawing steps is 75%-90%.
Based on above-mentioned purpose, we adopt Ni-38Cr-3Al-W to be main component on the Composition Design of alloy.This alloy is with Ni, Cr for basal component, and appropriate Al can separate out face-centered cubic γ ' strengthening phase (Ni with the Ni of matrix in aging strengthening model
3al), globular α-Cr phase is separated out in solution treatment process, the appropriate W added is solid-solution in matrix and separates out the WC of trace, 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 change 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, the therefore appropriate Al amount that contains particularly key.W participates in Precipitation behavior as solution strengthening element simultaneously, and increase intensity and the hardness of alloy, low-alloyed processing characteristics, falls in W too high levels.Y, as alloy purification element, 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, adds the alloying elements such as W, Y simultaneously in right amount and makes alloy have unique over-all properties.The composition of alloy of the present invention should control in (% by weight) Cr:37 ~ 38, Al:3.3 ~ 3.5, W:1.6 ~ 2.3, and 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 low NiCr alloy of hardness high magnetic, except alloying constituent, ensure that alloy property also needs to adopt the preparation method of the alloy such as suitable complete processing and thermal treatment process.
Prepare the non-magnetic nichrome of high rigidity of the present invention as follows:
1, melting
The surface oxide layer of W metal to be removed through polishing before molten alloy.Alloy melting will through vacuum induction and vacuum consumable duplex vacuum, vacuum tightness≤1 × 10
-1pa, strictly will control the scaling loss amount of alloying element in fusion process.
2, Homogenization Treatments
Alloy pig is placed in High Temperature Furnaces Heating Apparatus and carries out long-time homogenizing annealing process, strip off the skin after process and the chemical composition of sampling analysis alloy.
3, cogging, heat are pricked
Strip off the skin ingot cogging time lower than 600 DEG C of shove charges, the size of alloy pig determines the heat-up rate speed of alloy pig, starts to be forged into square billet after 1190 ~ 1210 DEG C of insulation appropriate times.Dish circle is rolled into again after 1190 ~ 1210 DEG C of insulation appropriate times.
4, solution heat treatment
Dish circle solution heat treatment temperature is 1180 ~ 1200 DEG C, is incubated 20 ~ 60 minutes, rapid hardening, obtains the single phase austenite tissue that crystal grain is tiny.Under the condition ensureing complete solid solution, then lower solid solubility temperature should be selected as far as possible.
5, cold drawn
Light bar is cold drawn to desired size by different cold deformation.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 aging strengthening model at 500-625 DEG C.
The NiCr alloy that the present invention relates to, on the basis of common nonmagnetic high-hardness alloy (domestic trade mark 3J40) composition, the content of suitable interpolation W and Y element, reduce Cr, put forward heavy alloyed hardness, coordinate by alloy cold deformation and aging temp the hardness regulating alloy, the NiCr alloy that 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, carries out cold drawnly carrying out 550 DEG C, 575 DEG C, 600 DEG C, 625 DEG C × 5h ageing treatment respectively, the hardness of the alloy after the solid solution+timeliness of gained afterwards to solid solution state alloy bar material;
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 DEG C 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 25Kg vacuum induction melting 2 (1#, 2#) compositions, the vacuum consumable electrode of 2 compositions prepared by consumable ingot after car light tack, and the high rigidity after vacuum consumable contrasts as shown in table 1 without magnetic NiCr alloy steel ingot and ripe trade mark product composition:
Table 1 alloying constituent
2, by alloy pig in 1200 DEG C through homogenizing annealing process in 1 hour, within 1 hour, square billet is forged in 1180 DEG C of insulations, square billet is rolled into Φ 10mm dish circle through 1180 DEG C of insulations after 1 hour, dish circle is hardening after 1200 DEG C 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 comparatively straight polishing.
3, carry out cold drawnly carrying out 550 DEG C, 575 DEG C, 600 DEG C, 625 DEG C × 5h ageing treatment respectively afterwards to solid solution state alloy bar material, 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 carrying out 500 DEG C of ageing treatment has performance as shown in Figure 3,4.
Coordinate suitable preparation technology by optimized alloy element, prepared there is premium properties high rigidity without magnetic nichrome.The hardness HRc > 60.5 of the solid solution aging state of development alloy, reach as high as 62, the hardness HRc > 65 of cold deformation aged, reaches as high as 67.5, volume susceptibility < 28 × 10
-6.
Claims (8)
1. high rigidity is without a magnetic nichrome, it 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 smeltings, Homogenization Treatments, cogging and hot rolling, solution treatment, cold drawn and ageing treatment step.
2. high rigidity according to claim 1 is without magnetic nichrome, it is characterized in that, this alloy described in using state metallographic structure is: the γ ' strengthening phase Ni of the austenitic matrix that crystal grain is tiny and precipitation
3the WC of Al, α-Cr phase and trace.
3. high rigidity according to claim 2 is without magnetic nichrome, it is characterized in that, described solution treatment obtains the tiny single phase austenite tissue of crystal grain.
4. high rigidity according to claim 1 is without magnetic nichrome, it is characterized in that, separates out globular α-Cr phase in described solution treatment process, and in ageing 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, comprise the steps:
1) batching also 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, and all the other are Ni; Adopt vacuum induction and the vacuum melting of vacuum consumable duplex, vacuum tightness≤1 × 10
-1pa;
2) homogenizing annealing process: alloy pig is placed in High Temperature Furnaces Heating Apparatus and is incubated 0.5-2 hour at 1100-1200 DEG C;
3) cogging, heat prick: strip off the skin ingot cogging time lower than 600 DEG C of shove charges, through 1190 ~ 1210 DEG C insulation 0.5-1 hour after be forged into square billet, then 1190 ~ 1210 DEG C insulation 0.5-1 hour after be rolled into dish circle;
4) solution treatment: be incubated 20 ~ 60 minutes at 1180 ~ 1200 DEG C, rapid hardening, obtains the single phase austenite tissue that crystal grain is tiny;
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 DEG C.
6. preparation method according to claim 5, is characterized in that, described solution treatment obtains the tiny single phase austenite tissue of crystal grain.
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 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 drawing steps is 75%-90%.
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| CN104233137B (en) * | 2014-08-26 | 2017-05-03 | 盐城市鑫洋电热材料有限公司 | Deformation and thermal treatment technology of nichrome 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 |
| CN105925849B (en) * | 2016-05-04 | 2017-10-13 | 中国第一重型机械股份公司 | A kind of control method of 700 DEG C of ultra-supercritical steam turbine rotors nickel-base alloy forging |
| 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 |
| CN108546834B (en) * | 2018-04-16 | 2020-02-07 | 北京科技大学 | Purification smelting method for nickel-based high-temperature alloy master alloy |
| 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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| CN1148097A (en) * | 1996-07-16 | 1997-04-23 | 冶金工业部钢铁研究总院 | High strength, nickel based and casted high temp. alloy |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| JPH07331369A (en) * | 1994-06-09 | 1995-12-19 | Sumitomo Metal Ind Ltd | Chronium-nickel-aluminum alloy for ultrahigh temperature use |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN1148097A (en) * | 1996-07-16 | 1997-04-23 | 冶金工业部钢铁研究总院 | High strength, nickel based and casted high temp. alloy |
Non-Patent Citations (2)
| Title |
|---|
| Ni-Cr-3%Al合金时效硬化性分析;陈丽华等;《东北大学学报（自然学报）》;19970630;第18卷(第3期);第270页第1-2段，倒数第2段 * |
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