CN1100160C - High-strength alloy with constant elasticity at high temp and its preparing process - Google Patents
High-strength alloy with constant elasticity at high temp and its preparing process Download PDFInfo
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- CN1100160C CN1100160C CN00134565A CN00134565A CN1100160C CN 1100160 C CN1100160 C CN 1100160C CN 00134565 A CN00134565 A CN 00134565A CN 00134565 A CN00134565 A CN 00134565A CN 1100160 C CN1100160 C CN 1100160C
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Abstract
The present invention belongs to the field of metallic functional structural materials, which is particularly to suitable for alloy materials for meters having a wide range of using temperature and requiring high strength and hardness and low temperature coefficient of elastic modulus in the range of the temperature for alloy. The alloy of the present invention has the components of 30 to 45% of Ni, 5 to 20% of Co, 2 to 6% of Nb, 0.5 to 3% of Ti and 0.5 to 5% of Cr, less than or equal to 0.5 % of Si, less than or equal to 0.1% of C, and Fe as the rest. Forging, rolling and annealing heat treatment are carried out for obtaining the better performance of the alloy, and a method is characterized in that solid solution heat treatment at a temperature of 980 DEG C to 1040 DEG C and time effect heat treatment at a temperature of 620 DEG C to 720 DEG C are carried out. Compared with the prior art, the steel of the present invention has the characteristics of wide range of using temperature, favorable comprehensive properties, etc.
Description
The invention belongs to metal function structured material field.Be specially adapted to that this alloy still has high intensity and hardness in wide temperature range, and lower permanent temperature coefficient of the elastic modulus.
As everyone knows, when constant modulus alloy normally is used as the elastic sensing element of precision instrument and mechanism and part, improve the operating accuracy of instrument by the temperature error that reduces instrument.General Fe-Ni, Ni-Co base ferromagnetic alloy (as 3J53,3J58) and Nb, Pd base paramagnetism alloy (as 55NbTiAl) all have low temperature coefficient of the elastic modulus in certain temperature range.But, for specific instrument, when requiring alloy to have lower temperature coefficient of the elastic modulus in wide temperature range, when requiring alloy to have high intensity and high hardness and good antioxidant property simultaneously, traditional constant modulus alloy just is difficult to satisfy its requirement again.General Fe-Ni base ferromagnetic alloy can only have low temperature coefficient of the elastic modulus in narrower temperature range, only be adapted at as the 3J53 alloy using in-60 ℃～80 ℃ the temperature range.To Nb base paramagnetism alloy (as 55NbTiAl), though its permanent elasticity temperature range than broad (can in 20 ℃～600 ℃ temperature ranges), but the temperature coefficient of the elastic modulus of this alloy higher (about 70～80 * 10
-6/ ℃).In addition, (the σ on the low side of the intensity behind the alloy aging
b＜1200MPa), plasticity is on the low side (δ＜5.5%).This can't satisfy specific service requirements.
The objective of the invention is to propose a kind of in the use temperature scope of broad, can have the high-strength alloy with constant elasticity at high temp of high intensity, hardness and lower permanent temperature coefficient of the elastic modulus and the manufacture method of this alloy thereof simultaneously.
Based on above-mentioned purpose, we at first are the magnetostrictive effects of utilizing the iron-nickel-cobalt ferromagnetic alloy when the design alloy ingredient, make alloy have low temperature coefficient of the elastic modulus and low frequency-temperature coefficient in wide temperature range.In the iron-nickel-cobalt alloy, add elements such as Ti, Nb again, guarantee to have high hardness and tensile strength after the alloy aging thermal treatment by timeliness diffusion-precipitation strengthening phase.Add a certain amount of chromium element then, the Young's modulus of alloy is improved, make of the susceptibility reduction of the temperature coefficient of the elastic modulus of alloy simultaneously alloying constituent.Adjust the rank of intensity, consistency and elasticity modulus temperature factor of alloy to satisfy special requirement by solid solution and timeliness thermal treatment again.Can make alloy through in-60 ℃～260 ℃ temperature ranges, having high hardness, high tensile strength and low temperature coefficient of the elastic modulus after different solid solutions and the timeliness thermal treatment simultaneously like this.
The high-strength alloy with constant elasticity at high temp that can in wide temperature range, use proposed by the invention, it is characterized in that the concrete Chemical Composition that this alloy is formed is (weight %) Ni 30-45%, Co 5-20%, Nb2-6%, Ti 0.5-3%, Cr 0.5-5%, Si≤0.5%, C≤0.1%, all the other are Fe.
She Ji basic alloy composition is Fe-Ni-Co in the present invention, is guaranteeing that this type of ferromagnetic alloy has high Curie temperature, thereby makes it have lower temperature coefficient of the elastic modulus in wide temperature range.In this composition, add dispersion-strengthened element nb (scope is elected 2-6% as), Ti (scope is elected 0.5-3% as) again, to guarantee the high strength and the hardness of alloy by timeliness thermal treatment diffusion-precipitation strengthening phase γ '.Because constant modulus alloy is very sensitive to chemical ingredients, add the Young's modulus and reduction temperature coefficient of the elastic modulus antioxidant property to alloying constituent responsive and raising alloy of certain Cr (scope is 0.5-5%) at last to increase alloy.The Si (＜0.5%) that can add trace in alloy is to separate out the temperature coefficient of the elastic modulus that sheet ε regulates alloy mutually by 720 ℃ of timeliness.When alloy smelting, can add micro-C (≤0.1%) with deoxidation.In addition, for the over-all properties that obtains in the composition of alloy of the present invention, the content of each element also can further be limit at (weight %) Ni 35-42%, Co8-17%, Nb 3-5.5%, Ti 1-2.5%, Cr 0.5-4.5%, all the other are Fe.
For high-strength alloy with constant elasticity at high temp of the present invention, can adopt conventional vacuum induction melting furnace, the alloy of melting all in the alloy ingredient of the present invention's design, sees Table 1 (embodiment of the invention).Vacuum melting technique requires vacuum tightness more than 1.33Pa.Starting material adopt the technical pure metal element, and purity should be greater than 99.8 weight %.The thermal treatment process that alloy ingot blank adopted 1100 ± 10 ℃ * 25 hours+1150 ± 25 ℃ * 24 hours is carried out homogenizing annealing and is handled.The laggard capable heats forged that descales is taken off on the alloy ingot blank surface.One fiery Forge Heating temperature is 1050 ± 10 ℃, is incubated 2 hours, and is incubated 2 hours in 800 ℃ in heat-processed.Two fiery Forge Heating temperature are 1030 ± 10 ℃, are incubated 30 fens.Final forging temperature is lower than 890 ℃.The forging deformation amount should be greater than 40%.It is the slab of 30mm that ingot casting becomes thickness through two fiery forging deformations.Slab carries out hot rolling after excluding the about 1.5mm of oxide skin.One heating process that rolls is during hot rolling: 1015 ± 5 ℃ * 1 hour, two heating processes that roll were: 1000 ± 5 ℃ * 30 minutes.Stopping rolling temperature should be less than 890 ℃, and deflection should be greater than 30%.Slab rolls into the made-up belt about 2.5mm the most at last.Surface scale is removed in made-up belt pickling after solution treatment in 1050 ℃ * 1 hour.Pickle solution is: HNO3: HCl=1: 5, add 50% water.Afterwards made-up belt is cold rolled to about 1.8mm thickness.Made-up belt finally is rolled down to desired thickness through annealing (annealing process is 1020 ± 5 ℃ * 1 hour, air cooling), cold rolling in vacuum oven (vacuum tightness of vacuum oven is higher than 7.466Pa) or gas shield stove then.Each cold rolling reduction can be controlled in 30-50%.
High-strength alloy with constant elasticity at high temp of the present invention is after above-mentioned melting, forging and cold and hot rolling processing; for obtain that good use properties is arranged in-60 ℃ of-260 ℃ of temperature ranges; carry out solution treatment, the solution treatment that it is characterized in that this alloy is in 980 ℃-1040 ℃ insulations 0.5-2 hour in vacuum or gas shield stove.Alloy grain size of the present invention after solution heat treatment should be less than 30 microns.Require and the requirement of hardness rank according to different use propertieies, alloy of the present invention is after solution treatment, and alloy strip steel rolled stock also should carry out timeliness thermal treatment in vacuum oven or gas shield stove.Be characterised in that requirement in addition in-60 ℃ of-260 ℃ of temperature ranges, above-mentioned alloy has and is lower than 40 * 10
-6/ ℃ temperature coefficient of the elastic modulus, require to be higher than the tensile strength and the hardness performance that is higher than HRC36 of 1250MPa simultaneously, it is characterized in that the ageing hot processing method that the alloy after solid solution adopts again is 720 ℃ of insulations 0.5-8 hour, be cooled to 620 ℃ of insulations 6-12 hour with stove.Also have in-60 ℃～260 ℃ temperature ranges alloy to have simultaneously and be lower than 60 * 10
-6/ ℃ temperature coefficient of the elastic modulus, be higher than the intensity of 1400MPa and be higher than HRC40 hardness, the ageing hot processing method of alloy should be 690 ℃ of insulations 6 to 10 hours, cools to 620 ℃ with stove then, is incubated 7 to 12 hours again.When above-mentioned solid solution and timeliness thermal treatment, adopt the vacuum tightness of vacuum oven should be higher than 7.466Pa in addition.Used shielding gas is argon gas or high pure nitrogen when adopting air protection method to carry out solid solution or timeliness thermal treatment.The alloy of the present invention that adopts the inventive method to produce, after different solid-solution and aging heat treatment, this alloy structure mainly is made of mutually γ matrix phase, γ ' dispersion-strengthened phase, crystal boundary LAVES, and a spot of sheet ε phase also may have been observed in the part.
The alloy that adopts alloy preparation method of the present invention to produce has the alloy good combination property compared with prior art, characteristics such as use temperature wide ranges, intensity, hardness height and good in oxidation resistance, this alloy is made into device, use is in instrument, can improve the operating accuracy of instrument, thereby satisfy the various requirement that the user proposes.
Embodiment
We adopt high-strength alloy with constant elasticity at high temp of the present invention to do the test of five composition parts altogether, for with the prior art alloy ratio, two groups of contrast compositions have also been done simultaneously, see Table 1, sequence number 1,2,3,4,5 is alloy ingredient of the present invention in each table of embodiment, sequence number 5 is comparative alloy 3J53, and sequence number 6 is comparative alloy 55NbTiAl.The melting of above-mentioned alloy is all carried out in vacuum induction furnace, and vacuum tightness is more than 1.33Pa.Alloy ingot blank was through annealing in 1100 ℃ * 25 hours, and is cold in 1150 ℃ * 24 hours annealing back stoves again.Forge after ingot blank after homogenizing annealing is handled should remove oxide skin, a fiery forging temperature is 1050 ℃ * 2 hours again, and is incubated 2 hours in 800 ℃ in heat-processed.Two fiery forging temperatures are 1030 ℃ * 0.5 hour, and final forging temperature should be below 890 ℃, and the forging deformation amount is greater than 40%.In the operation of rolling, one to roll temperature be 1015 ℃ * 1 hour, and two to roll temperature be 1000 ℃ * 0.5 hour, and final forging temperature should be at 830 ℃, and deflection is 35%.Through pickling and vacuum annealing, its vacuum tightness is 7.466Pa then.Annealing process is that temperature is that stove is cold after 1020 ℃ * 1 hour.The solid solution of alloy of the present invention, aging thermal treating process and corresponding see Table 2, performance comparison sees Table 3.
Aging technique corresponding in table 2 is numbered: 1#620 ℃ is incubated 8 hours, and stove is cold.2#720 ℃ is incubated 8 hours, furnace cooling to 620 ℃ insulation 6 hours, and stove is cold.3#720 ℃ is incubated 5 hours, furnace cooling to 620 ℃ insulation 10 hours, and stove is cold.4#690 ℃ is incubated 10 hours, furnace cooling to 620 ℃ insulation 9 hours, and stove is cold.5#690 ℃ is incubated 6 hours, furnace cooling to 620 ℃ insulation 12 hours, and stove is cold.6#690 ℃ is incubated 10 hours, furnace cooling to 620 ℃ insulation 7 hours, and stove is cold.At the neutral energy unit of table 2 being in addition | β E| is the temperature coefficient of the elastic modulus in-60 ℃ of-260 ℃ of temperature ranges, and unit is * 10
-6/ ℃.Stretching bullet degree unit is MPa.Stretch percentage elongation unit is %.Shown in the table 3 among the alloy embodiment of the present invention the gentle 5NbTiAl of 3J53 of the performance of sequence number 3 and Comparative Examples sequence number 5,6 carry out performance relatively.In foregoing, table 1 is the composition contrast of the embodiment of the invention and prior art.Table 2 is the invention process solid solution, aging thermal treating process and performance table, and table 3 is shown compared with the prior art for the performance in the embodiment of the invention.
Table 1. embodiment of the invention and prior art alloying constituent be (weight %) relatively
| Preface is led | Principal element | Ni | Co | Nb | Ti | Si | Cr | C | Al | Fe |
| 1 | 1 | 35.0 | 8.0 | 3.0 | 1.2 | 0 | 0.5 | 0.01 | 0.003 | All the other |
| 2 | 2 | 37.5 | 11.2 | 4.2 | 1.0 | 0.2 | 1.5 | 0.01 | 0.005 | All the other |
| 3 | 3 | 38.2 | 13.6 | 4.8 | 1.7 | 0.4 | 1.9 | 0.015 | 0.007 | All the other |
| 4 | 4 | 40.5 | 15.2 | 4.2 | 2.0 | 0.5 | 2.5 | 0.02 | 0.006 | All the other |
| 5 | 5 | 42.0 | 17.0 | 5.5 | 2.5 | 0 | 4.5 | 0.02 | 0.008 | All the other |
| 6 | 3J53 | 41.5-4 | - | - | 2.3-2.7 | ＜0.8 | 5.2-5.8 | ＜0.05 | 0.5-0.8 | All the other |
| 7 | 55NbTiAl | - | - | 55.0 | 39.5 | - | - | - | 5.5 | - |
Table 2. alloy of the present invention gained performance behind different solid solutions, aging thermal treating process
The comparison of table 3. alloy of the present invention and prior art constant modulus alloy salient features
| Sequence number | Performance | 980 ° of solid solutions 1 hour | 980 ° of solid solutions 2 hours | 1000 ° of solid solutions 1 hour | 1020 ° of solid solutions 1 hour | 1040 ° of solid solutions 30 minutes | |||||
| 1# technology timeliness | 2# technology timeliness | 3# technology timeliness | 4# technology timeliness | 1# technology timeliness | 4# technology timeliness | 5# technology timeliness | 6# technology timeliness | 4# technology timeliness | 6# technology timeliness | ||
| 1 | |β E|，×10 -6/℃ | 35.5 | 38.8 | 37.5 | 45.3 | 36.5 | 45.9 | 46.3 | 43.5 | 48.9 | 43.2 |
| Tensile strength, MPa | 1250 | 1258 | 1280 | 1480 | 1240 | 1470 | 1420 | 1403 | 1430 | 1405 | |
| HRC | 36.5 | 35.7 | 37.5 | 42.8 | 35.0 | 41.3 | 40.9 | 40.2 | 40.7 | 41.0 | |
| Unit elongation, % | 20.0 | 18.6 | 19.3 | 17.0 | 21.3 | 18.2 | 19.2 | 19.9 | 20.1 | 20.3 | |
| 2 | |β E|，×10 -6/℃ | 39.2 | 39.7 | 39.0 | 47.8 | 39.0 | 48.5 | 49.2 | 48.7 | 49.6 | 47.9 |
| Tensile strength, MPa | 1290 | 1300 | 1310 | 1498 | 1273 | 1459 | 1420 | 1415 | 1432 | 1400 | |
| HRC | 37.5 | 38.6 | 38.7 | 43.5 | 36.5 | 42.2 | 41.3 | 41.0 | 41.7 | 40.2 | |
| Unit elongation, % | 18.3 | 17.0 | 17.8 | 16.7 | 19.7 | 17.8 | 19.7 | 20.3 | 18.7 | 19.7 | |
| 3 | |β E|，×10 -6/℃ | 38.7 | 38.5 | 37.6 | 55.4 | 37.8 | 57.4 | 58.3 | 56.2 | 58.6 | 55.8 |
| Tensile strength, MPa | 1345 | 1358 | 1398 | 1540 | 1335 | 1510 | 1476 | 1450 | 1479 | 1455 | |
| HRC | 39.5 | 40.1 | 41.2 | 46.5 | 37.2 | 45.2 | 43.2 | 42.8 | 44.5 | 43.0 | |
| Unit elongation, % | 16.0 | 15.4 | 15.8 | 14.0 | 17.3 | 14.9 | 16.5 | 17.5 | 15.2 | 18.2 | |
| 4 | |β E|，×10 -6/℃ | 39.8 | 39.3 | 38.6 | 59.6 | 38.9 | 58.6 | 59.7 | 57.9 | 59.3 | 56.0 |
| Tensile strength, MPa | 1350 | 1368 | 1390 | 1570 | 1332 | 1510 | 1497 | 1473 | 1489 | 1480 | |
| HRC | 37.6 | 40.5 | 41.8 | 47.4 | 38.2 | 46.8 | 44.9 | 43.0 | 45.3 | 44.1 | |
| Unit elongation, % | 16.5 | 15.6 | 14.3 | 10.3 | 17.5 | 11.2 | 11.7 | 12.1 | 12.7 | 12.9 | |
| 5 | |β E|，×10 -6/℃ | 37.5 | 36.3 | 38.7 | 58.4 | 38.5 | 57.3 | 58.2 | 54.3 | 58.3 | 55.2 |
| Tensile strength, MPa | 1420 | 1390 | 1480 | 1620 | 1389 | 1589 | 1573 | 1561 | 1578 | 1568 | |
| HRC | 41.0 | 42.5 | 43.9 | 48.8 | 40.2 | 47.2 | 46.9 | 45.7 | 47.8 | 48.2 | |
| Unit elongation, % | 13.0 | 16.2 | 13.8 | 8.9 | 10.8 | 9.7 | 10.2 | 11.3 | 9.7 | 12.1 | |
| Alloy | Materials behavior and shape | The use temperature scope | In the use temperature scope | β E| value, * 10 -6/℃ | Tensile strength MPa | Unit elongation % |
| Embodiment 3 alloys | 1000 ℃, solid solution in 1 hour, 1# aging technique timeliness, band | -60～260℃ | 37.8 | 1335 | 17.3 |
| 1020 ℃, solid solution in 1 hour, 4# aging technique timeliness, band | -60～260℃ | 55.8 | 1545 | 14.2 | |
| 3J53 | Solid solution, 650 ℃ of timeliness, band | -60～80℃ | 46 | 1079 | 10.0 |
| Cold rolling, 650 ℃ of timeliness, band | -60～80℃ | 15 | 1226 | 6.0 | |
| 55NbTiAl | 1000 ℃ of solid solutions, 650 ℃ of timeliness 10 hours, band | 20℃～600℃ | 70～80 | 1059 | 2.5 |
| 35% cold deformation, 650 ℃ of timeliness 10 hours, band | 1147 | Brittle failure |
Claims (10)
- One kind can be in wide temperature range (60 ℃～260 ℃) high-strength constant modulus alloy of using, it is characterized in that concrete Chemical Composition at alloy is that (weight %) Ni is that 30-45%, Co are that 5-20%, Nb are that 2-6%, Ti are that 0.5-3%, Cr are that 0.5-5%, Si≤0.5%, C≤0.1%, surplus are Fe.
- 2. alloy according to claim 1 is characterized in that the Ni content in this alloy is 35-42%.
- 3. alloy according to claim 1 is characterized in that Co content is 8-17% in this alloy.
- 4. alloy according to claim 1 is characterized in that Nb content is 3-5.5% in this alloy.
- 5. alloy according to claim 1 is characterized in that Ti content is 1-2.5% in this alloy.
- 6. alloy according to claim 1 is characterized in that Cr content is 0.5-4.5% in this alloy.
- 7, manufacture method according to the described high-strength alloy with constant elasticity at high temp that (60 ℃～260 ℃) use in wide temperature range of claim 1, the homogenizing annealing that ingot casting base after the vacuum melting carried out 1100 ± 10 ℃ * 25 hours+1150 ± 25 ℃ * 24 hours is handled, one fiery Forge Heating temperature is 1050 ± 10 ℃ of insulations 2 hours, and in heat-processed, be incubated 2 hours in 800 ℃, two fiery Forge Heating temperature are 1030 ± 10 ℃ of insulations 0.5 hour, final forging temperature is lower than 890 ℃ of forging deformation amounts should be greater than 40%, one burning hot roll process is 1015 ± 5 ℃ * 1 hour, two burning hot roll process are 1000 ± 5 ℃ * 0.5 hour, stopping rolling temperature should should be greater than 30% less than 890 ℃ of deflections, is HNO at pickle solution after handling in 1050 ℃ * 1 hour 3: HCl=1: carry out pickling in 5, strip off the skin again cold rolling; each cold rolling reduction is controlled at 30-50%; the solution heat treatment of this alloy is to carry out in vacuum or gas shield stove, and the technology of its solution heat treatment is: 980 ℃ of-1040 ℃ of soaking times are 0.5-1.5 hour.
- 8, according to the manufacture method of described this alloy of claim 7, the aging thermal treating process that alloy adopted of its feature after solution treatment is: 720 ℃ of insulations 0.5-8 hour are incubated 6-12 hour during furnace cooling to 620 ℃ then again.
- 9, according to the manufacture method of described this alloy of claim 7, the aging thermal treating process that alloy adopted of its feature after solution treatment is: 690 ℃ of insulations 6-12 hour are incubated 7-12 hour during furnace cooling to 620 ℃ then again.
- 10, according to the manufacture method of claim 7,8,9 described these alloys, it is characterized in that solid solution, timeliness thermal treatment are to carry out in vacuum oven, its vacuum tightness should be greater than 7.466pa.
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Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN100460547C (en) * | 2006-12-08 | 2009-02-11 | 重庆仪表材料研究所 | High-temperature-resistance FeNiCo constant-modulus alloy, its preparation method, and method for preparing components by using same |
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| CN100537818C (en) * | 2008-05-29 | 2009-09-09 | 钢铁研究总院 | A kind of constant modulus alloy with high magnetic induction and low frequency temperature coefficient |
| CN105671282A (en) * | 2014-11-20 | 2016-06-15 | 中国航空工业第六八研究所 | Stabilization treatment method for high-elasticity alloy microgroove part |
| CN106269867A (en) * | 2015-06-08 | 2017-01-04 | 丹阳市凯鑫合金材料有限公司 | The ingot hot rolling of a kind of invar side that cost is relatively low and efficiency is higher makes the method for pipe |
| CN107739998B (en) * | 2017-10-16 | 2019-06-21 | 攀钢集团江油长城特殊钢有限公司 | A kind of preparation method of flat cold-rolled sheet |
| CN112813328A (en) * | 2020-12-30 | 2021-05-18 | 大连理工大学 | High-entropy alloy with excellent room temperature and low temperature performance and preparation method thereof |
| CN114351006B (en) * | 2022-01-10 | 2023-02-07 | 深圳市飞亚达精密科技有限公司 | Constant-elasticity alloy material, application and preparation method thereof, and manufacturing method of balance spring |
| CN117867245B (en) * | 2024-03-11 | 2024-06-04 | 成都先进金属材料产业技术研究院股份有限公司 | High-temperature alloy plate and preparation method thereof |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1040626A (en) * | 1988-08-22 | 1990-03-21 | 冶金工业部钢铁研究总院 | Maraging steel and manufacture method thereof |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1040626A (en) * | 1988-08-22 | 1990-03-21 | 冶金工业部钢铁研究总院 | Maraging steel and manufacture method thereof |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN100460547C (en) * | 2006-12-08 | 2009-02-11 | 重庆仪表材料研究所 | High-temperature-resistance FeNiCo constant-modulus alloy, its preparation method, and method for preparing components by using same |
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| CN1305021A (en) | 2001-07-25 |
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