CN1455014A - Thermal-resistance tool - Google Patents
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Abstract
The invention relates to a thermal-resistance tool, and a method for producing the object with good hardness under high heat. According to the invention, the tool or object comprises Fe-Co-W/Mo- high speed cutting alloy, as tool material, containing, based on weight percent, Co 15.0-30.0; W 4.0-30.0; Mo 6.0-22.0, in which W+2Mo=18.0-49.0; C 0.005-0.19; N 0.01-0.1; V, Nb, Ti, Zr and Ta: the individual element or the combination is 0.12-0.9. Fe, based on the refining condition, is the residuel impurity. The tool material, produced by the method of powder meltallurgy, can be hardened by solutionizing treatment after forming the tool and sequently cooling at the room temperature and then precipitation treatment, having the rigidity of more than 65 HRC.
Description
The present invention relates to a kind of Thermal-resistance tool, especially for the instrument of machining austenitic steel, nickel-base alloy and titanium material.
The invention still further relates to the method that is used to prepare object in addition with high hot hardness.
The instrument that is used for interrupted processing or the continuous processing work of free of discontinuities all should have high rigidity and high wearing resistance.
Just known for a long time, carbonaceous ferrous alloy is used as tool material, and its hardness improves by form martensite in weave construction as required through quenching sclerosis.In this hardening process, be basically under the temperature that has improved to the cooling and carry out the transformation of the nothing diffusion of microtexture fast of material with centroid cubic lattice structure.Form martensitic atom and transfer to new weave construction from the austenite crystallographic site, the professional also is referred to as the upset-transformation in quenching process.
The heat treating method that is added into other alloying element in the carbonaceous iron and uses tailor-make allows to prepare thus object or instrument, its the quenching transformation of structure or heat turn over become change after, yet after annealing immediately, have high desired mechanical property and similar use properties value according to circumstances.
The structure that obtains by transformation when the austenitic solid solution range of cooling does not show thermodynamically stable equilibrium state.Be heated to the temperature that generates more than the temperature, or under this temperature long time treatment, structure changes so that the performance of material changes.
In other words: when high temperature occurring in the work area in the actual use at instrument, material hardness can descend in this zone, and the reduction of its use properties therefore occurs.
In order to improve the workpiece Economics of Processing, present purpose is the instrument that preparation has the material through having improved hot hardness.If tool material have carbide or other hardness of matter in structure, this notion of hot hardness just relates to body portion so.
Known, opposite with the quench hardening that forms feature with martensite, precipitation hardening is without this realization.Prerequisite for precipitation hardening is the solubleness that the alloy additive in matrix metal descends along with temperature.
In precipitation hardening, the alloying material of solution treatment carries out more intensive cooling immediately.In the solution treatment under higher temperature, a kind of alloy additive or a phase in material completely or partially are added in the solution, and are quenched to room temperature and become the supersaturation solution.When the temperature that is heated to immediately below the solid solution temperature, partly being precipitated out of alloy additive or phase with the corresponding supersaturation of temperature, this produces material property to change.Can prepare the alloy that has permanent magnetism or have high rigidity like this.
So the present task of the present invention is, prepare a kind of Thermal-resistance tool, the body portion of its material or material has at high temperature bigger than the hardness of rapid steel hardness, the metamorphism of instrument do not occur by sclerosis at this.In addition, even also can keep the hardness of material under the heat effect for a long time in the work area of instrument, and therefore also allow do not have or the situation of less cooling of tool under and with higher interruption speed cutting.Final task of the present invention provides the cutting material that is used for free of discontinuities processing austenitic alloy, the cutting material of for example antirust Cr-Ni-steel, nickel-base alloy and titanium material, this cutting material make to have high suface processing quality, the economic possibility that is processed under high life tools.
This task solves by a kind of Thermal-resistance tool, is made of the high speed cutting alloy that contains iron-cobalt-tungsten and molybdenum, in weight %
Cobalt (Co) 15.0-30.0
Tungsten (W) 4.0-30.0
Molybdenum (Mo) 6.0-22.0
Condition is that the content of tungsten adds that the content of 2 times of molybdenums is 18.0-49.0
(W+2Mo=18.0 to 49.0)
Carbon (C) 0.005-0.19
Nitrogen (N) 0.01-0.1
Be limited to 0.85 on the aluminium (Al)
Be limited to 0.85 on the silicon (Si)
Condition is that the content of aluminium adds that the content of silicon is up to 0.95
(Al+Si)???≤0.95
Nickel (Ni)＜0.4
Manganese (Mn)＜0.4
Chromium (Cr)＜1.3
Iron and by the refining conditional decision as the impurity of surplus, as tool material, its mode with powder metallurgy is passed through with nitrogen the alloy atomization powdered, use hot isostatic pressing method (HIPen) that powder is pressed into preformed material immediately, and thermal distortion and/or the cold deformation by preformed material prepares according to circumstances, so the later instrument of moulding by solution treatment and be cooled to room temperature immediately and subsequently precipitation process harden, and have hardness greater than 65HRC.
The advantage that reaches by the present invention particularly in, significant temp is under 650 ℃ in long-time, the hardness value that instrument reaches is compared much higher with known efficient high-speed steel.Follow according to alloy technology of the present invention with the technology of preparing feature be important at this.
The Fe-Co-W/Mo-alloy changes face-centered cubic (α)-atomic structure into from body-centered cubic (γ) under heating in certain concentration range, wherein the height of transition temperature depends on the composition that alloy is current.Small in the α-zone of alloy with the solubleness of the sedimentary element of formation of temperature correlation respectively at this, it has raising in γ-zone on the contrary.
In having the alloy of low carbon content, tungsten and molybdenum cause precipitation hardening, and enter the intermetallic phase from the supersaturation solution is most.These elements in fact similarly influence the stability of the particle of transition temperature and metalloid to cohesion, and then influence the hardness and the thermotolerance of material.Along with the total content of these elements is brought up to 49 weight %, secondary hardness and thermotolerance increase.No longer improve these performances for higher content owing to the growth of metalloid, in contrast, during for the element that is lower than 18.0 weight % (W+Mo) concentration, intensity of measuring and material toughness decline to a great extent.
The alloying element cobalt produces complicated influence to material property.Part cobalt by form metalloid (Fe, Co)
7(W, Mo)
6And the participation precipitation hardening has so just reduced its concentration in α-mutually.Another part cobalt has guaranteed the recrystallization of alloy.When being lower than 19.0 weight % for cobalt contents, even a part of weave construction also remains under high heating among the α-mutually, material is stablized coarse grained that ferritic effect becomes and do not expect owing to W and Mo.When being higher than 25 weight % for cobalt contents, the amount of metalloid increases, and the mechanical property that causes material reduces can not further improving under hardness and the stable on heating situation.
When the scope of the share of molybdenum contrast tungsten composition, improved the intensity of Fe-Co-W/Mo-alloy significantly at 4.0-30.0 weight %, and to the almost not influence of its α-γ-transition temperature.Obtain hardness, intensity and stable on heating best of breed in tungsten than molybdenum is the proportional range of 0.7-1.6, at this, the minimum content of molybdenum in alloy should be 7.0 weight %.Make the precipitation exquisiteness and the homogeneous of metalloid primely until the molybdenum of 18.0 weight %.
Though carbon forms (M to the not influence of transition temperature of alloy when being higher than the concentration of 0.16 weight %
6C) carbide of class, it is not having to reduce hardness, thermotolerance and the cutting ability of instrument under the further alloy technology measure.Carbon content will delay sedimentary formation when being lower than 0.008 weight %, thus as find that the carbon content in the alloy that according to circumstances matrix constitutes should be 0.008-0.16 weight %.
0.01-0.1 the nitrogen of weight % is because the formation nitride is favourable, and the fineness and the uniformity of promotion weave construction.
The combination of vanadium, niobium, tantalum, titanium and zirconium individual element or these elements is technical superior fine granular and bonding carbon and the nitrogen in be far from dissolved carbide and nitride especially that is used for forming.These elements of concentration range by 0.14-0.9 can improve the state of grain boundary in addition, and this can improve the toughness of material.
Though aluminium and silicon have improved the α-γ-transition temperature of alloy and have improved the performance of material, but also stablized ferrite, so the content of preferred aluminium should not surpass 0.85 weight %, the content of silicon should not surpass 0.85 weight %, and their total content should not surpass 0.95 weight %.
When the content of nickel and manganese during greater than 1.3 weight %, though improved the mechanical property of material, has also reduced the thermotolerance of instrument greater than the content of 0.4 weight % and chromium.
Known powder metallurgy own prepares preformed material also invention.Show, by with nitrogen to the alloy gas jet, with being about to the compacting of powder hot isostatic pressing, the performance of stampings is to regulate easily, and the height uniformity of alloying elements distribution and in preformed material segregation-free be attainable.Find that in addition the PM-technology plays favourable and purified effect to precipitation kinetics and sedimentary morphology, this is not also had known scientific explarnation.
According to the present invention, by until the annealing of about 650 ℃ precipitation, do not cause tool variations or deformation just hardness can be brought up to hardness value greater than 65HRC, this instrument that just makes does not need or only needs less precision work.
Superior composition form of the present invention is indicated in claim 2.
Special in the high rigidity under the good toughness values of material, following situation is favourable, if promptly in tool material, formed precipitation has 1-5 μ m mean size, have basically (Fe, Co)
7(W, Mo)
6Structure.
In order to reach the further additional wear resistance that improves of Thermal-resistance tool, a form of implementation according to the present invention is drafted, and in having the matrix of above-mentioned feature, with the amount until 28 volume %, with the form of fine distribution the sclerosis phase is set in heterogeneity in material.
The desired task of the present invention in being included in solves in a method that is used for preparing the object with high hot hardness, and promptly in this method, preparation has the molten metal of following moiety in weight %
Cobalt (Co) 15.0-30.0
Tungsten (W) 4.0-30.0
Molybdenum (Mo) 6.0-22.0
Condition is that the content of tungsten adds that the content of 2 times of molybdenums is 18.0-49.0
(W+2Mo＝18.0-49.0)
Carbon (C) 0.005-0.19
Nitrogen (N) 0.01-0.1
Be limited to 0.85 on the aluminium (Al)
Be limited to 0.85 on the silicon (Si)
Condition is that the content of aluminium adds that the content of silicon is up to 0.95
(Al+Si)???≤0.95
Nickel (Ni)＜0.4
Manganese (Mn)＜0.4
Chromium (Cr)＜1.3
Make iron and by the refining conditional decision as the impurity of surplus, through nitrogen molten metal is atomized into metal-powder, afterwards, this powdered alloy is pressed into preformed material with hot isostatic pressing method, this preformed material carries out thermal distortion according to circumstances under 1200-950 ℃, the result further is processed into the object matrix, after the final molding, carry out solution treatment being higher than under 1200-1300 ℃ the temperature, quench immediately and 500-650 ℃ of following precipitation hardening annealing, the hardness of object reaches the hardness value that is higher than 65HRC like this.
The resulting advantage of the method according to this invention particularly in, the molten metal that further processing and mechanical property at high temperature have best moiety is considered in preparation.Like this, using nitrogen can obtain for the high homogeneous best result of material as the preformed material of exhalation medium according to powder-metal-technology preparation, under at least 950 ℃ temperature, can improve the thermoplasticity of material, yet also support thermoplasticity from 1000 ℃ to 1200 ℃ with under the higher temperature.After the last moulding of object, can carry out solution treatment being higher than under 1200-1300 ℃ the temperature, there be not the cooling at room temperature forced under the warpage in an advantageous manner immediately, also under 500-670 ℃, be preferably and carry out precipitation hardening to material hardness under the situation that does not cause part distortion until 650 ℃ and be higher than 65HRC.Because according to the present invention, element Ni and Mn have upper limit concentration in material, and promote the element Cr of hardening capacity to be adjusted to maximum level, so can realize high α-γ-transition temperature and high thus material hardness and add the maximum life span of instrument in man-hour in the free of discontinuities of metallic substance.And have until the C of 1.7 weight % and the carbide that reduces wear of high share, particularly the high alloy rapid steel of single carbide is compared, according to instrument of the present invention, throw is adding instrument or rather, provide the free of discontinuities performance that has improved 89 coefficients when the high alloy austenite oil field parts ( lfeldkomponenten) of high corrosion resistance are arranged, this also is higher than the performance of carbamide tool.
The feature of indicating by claim 6 is implemented in the frequency of the top temperature stability of the assurance that reaches degree of certainty under the high-mechanical property value and precipitation hardening.
In the further formation of the method according to this invention, following situation is superior, promptly make alloy when molten metal and the additional moiety that has chosen, these moietys are until the carbon of 1 weight % with until the nitrogen of 0.2 weight % with form single carbide-and the elemental vanadium of nitride, niobium, tantalum, titanium and zirconium, they are one, or the total content of combination is until 2.45 weight %, at this, the single carbide of the content of simple substance carbon and nitrogen element and its formation-or-ratio of the element of nitride is respectively 0.4-0.46, with hardened object by the precipitation of intermetallic phase, for example (Fe, Co)
7(W, Mo)
6With harden by the carbide of fine dispersion and/or so sedimentary overlapping covering of nitride or special nitride.This two-or the two-phase sclerosis this advantage is arranged, promptly by the sclerosis of the metalloid high-temperature stable overlapping covering by a kind of secondary hardening that is similar to carbide precipitation hardened Thermal-resistance tool steel, the mechanical high-temperature behavior of formed like this object further improves.
This also is possible, promptly further improve high-wearing feature through the material of precipitation hardening, before the container compacting, add total amount until one or more powder sizes of 28 volume % hard material powder if be used for the metal-powder through nitrogen atomization of hot isostatic pressing compacting until 5 μ m, and in container homogeneous distribution.The advantage that is reached mainly is like this, and hard material powder is ectogenic, for the not influence of optimizing of matrix moiety.
As shown in Figure 1, according to softening test following at 650 ℃ and time correlation, compare according to sample of the present invention and these rapid steel samples according to prior art.
In table 1, provided sample material chemical ingredients separately.Table 2 has provided the heat treatment parameter and the hardness value of the sample of being tested.
The bill of material that is used for instrument according to the present invention reveals more superior hot hardness in Fig. 1.Move towards with time relation in this surface hardness (measure according to bounce-back-testing method under test temperature, calculate) that has demonstrated at 650 ℃ of following samples according to DIN 51303-1975 or JIS 7731-1976.Particularly after greater than 10 minutes time, recording obviously much smaller hardness decline under 650 ℃ for material according to the invention.
| ?C | ?Si | ?Mn | ?P | ?S | ?Cr | ?Mo | ?Ni | ?V | ?W | ?Co | ?Cu | ?Al | ?Nb | ?Ti | ?Zr | ? | N | |
| Alloy | ||||||||||||||||||
| 1 | ?0.14 | ?0.27 | ?0.23 | ?0.008 | ＜0.004 | ?0.64 | ?6.9 | ?0.11 | ?0.65 | ?10.1 | ?24.8 | ＜0.03 | ?0.04 | ?0.03 | ＜0.01 | ?0.02 | ?0.02 | 0.04 |
| Alloy 2 | ?0.08 | ?0.25 | ?0.14 | ?0.009 | ＜0.004 | ?0.44 | ?8.9 | ＜0.10 | ?0.45 | ?10 | ?25.7 | ＜0.03 | ?0.13 | ?0.1 | ?0.03 | ＜0.01 | ＜0.01 | 0.055 |
| | ?1.65 | ?0.5 | ?0.22 | ?0.02 | ?0.018 | ?4.52 | ?2.21 | ?0.28 | ?4.88 | ?10.75 | ?8.01 | ?0.11 | ＜0.005 | ?0.01 | Trace | Trace | Trace | 0.051 |
| Rapid steel 2 | ?2.29 | ?0.62 | ?0.28 | ?0.02 | ?0.002 | ?4.23 | ?6.52 | ?0.29 | ?6.15 | ?6.32 | ?10.26 | ?0.12 | ＜0.005 | ?0.021 | Trace | Trace | Trace | 0.074 |
| Rapid steel 3 | ?3.43 | ?0.61 | ?0.38 | ?0.013 | ?0.016 | ?4.02 | ?4.81 | ?0.31 | ?9.51 | ?9.91 | ?8.46 | ?0.11 | ＜0.005 | ?0.009 | Trace | Trace | Trace | 0.045 |
Table 1: the chemical ingredients of test material
| Hardness | Annealing | Initial hardness [HRc] | |
| | 1250 ℃-salt bath-oil | 3 * 580 ℃ (every 2h) | 67.9 |
| Alloy 2 | 1250 ℃-salt bath-oil | 3 * 610 ℃ (every 2h) | 65.5 |
| | 1190 ℃/vacuum | 3 * 540 ℃ (every 2h) | 66.5 |
| Rapid steel 2 | 1190 ℃/vacuum | 3 * 580 ℃ (every 2h) | 66.1 |
| Rapid steel 3 | 1190 ℃/vacuum | 3 * 580 ℃ (every 2h) | 67.3 |
Table 2: the thermal treatment of test material
Claims (8)
1. Thermal-resistance tool, especially for the instrument of the material of processing austenitic steel, nickel-base alloy without interruption and being made of titanium, it is made of the Fe-Co-W/Mo-high speed cutting alloy that contains following composition in weight %
Cobalt (Co) 15.0-30.0
Tungsten (W) 4.0-30.0
Molybdenum (Mo) 6.0-22.0
Condition is that the content of tungsten adds that the content of 2 times of molybdenums is 18.0-49.0
(W+2Mo=18.0 to 49.0)
Carbon (C) 0.005-0.19
Nitrogen (N 0.01-0.1
Be limited to 0.85 on the aluminium (Al)
Be limited to 0.85 on the silicon (Si)
Condition is that the content of aluminium adds that the content of silicon is up to 0.95
(Al+Si)??≤0.95
Nickel (Ni)＜0.4
Manganese (Mn)＜0.4
Chromium (Cr)＜1.3
Iron and by the refining conditional decision as the impurity of surplus, as tool material, its mode with powder metallurgy is passed through with nitrogen the alloy atomization powdered, use hot isostatic pressing method (HIPen) that powder is pressed into preformed material immediately, and thermal distortion and/or the cold deformation by preformed material prepares according to circumstances, so the later instrument of moulding by solution treatment and be cooled to room temperature immediately and subsequently precipitation process harden, and have hardness greater than 65HRC.
2. according to the Thermal-resistance tool of claim 1, one or more elements of its high speed cutting alloy or element set are limited in the following concentration range in weight %,
Co 19.0-25.0 is preferably 20.0-23.0
W???????????10.0-25.0
Mo 0.7-18.0 is preferably 8.0-14.0
W+2Mo 22.0-34.0 is preferably 24.0-28.0
C 0.008-0.16 is preferably 0.01-0.14
N 0.02-0.08 is preferably 0.025-0.068
V, Nb, Ti, Zr, Ta (combinations of individual element or these elements)
0.14-0.8, be preferably 0.15-0.5
Be limited to 0.7 on the Al, be limited to 0.5 on preferred
Si 0.12-0.6 is preferably 0.15-0.5
Al+Si 0.12-0.8 is preferably 0.15-0.6
Ni＜0.3, be preferably＜0.2
Mn＜0.3, be preferably＜0.2
Cr＜1.2, be preferably＜0.9
3. according to the Thermal-resistance tool of claim 1 or 2, it is 1-5 μ m that its formed precipitation in tool material has mean particle size, is preferably 2-3.6 μ m, have basically and be (Fe, Co)
7(W, Mo)
6Structure.
4. have the Thermal-resistance tool according to the matrix of claim 1-3, it contains total amount to 28 volume %, is preferably below 20 volume %, is preferably the hard phase of the homogeneous distribution therein between the 5-15 volume % especially.
5. method that is used for preparing object with high hot hardness, particularly have austenitic iron-and the preparation method of the Thermal-resistance tool of the high free of discontinuities performance of nickel-Ji and titanium material, in the method, preparation has the molten metal of following moiety in weight %
Cobalt (Co) 15.0-30.0
Tungsten (W) 4.0-30.0
Molybdenum (Mo) 6.0-22.0
Condition is that the content of tungsten adds that the content of 2 times of molybdenums is 18.0-49.0
(W+2Mo=18.0 to 49.0)
Carbon (C) 0.005-0.19
Nitrogen (N) 0.01-0.1
Be limited to 0.85 on the aluminium (Al)
Be limited to 0.85 on the silicon (Si)
Condition is that the content of aluminium adds that the content of silicon is up to 0.95
(Al+Si)????≤0.95
Nickel (Ni)＜0.4
Manganese (Mn)＜0.4
Chromium (Cr)＜1.3
Make iron and by the refining conditional decision as the impurity of surplus, by with nitrogen to the jet one-tenth metal-powder of molten metal, afterwards, the powdered alloy hot isostatic pressing method is pressed into preformed material and carries out possible thermal distortion under 1200-950 ℃, further be processed into the object matrix with being about to it, this object matrix is after final molding, in being higher than 1200-1300 ℃ temperature range, carry out solution treatment, quench immediately and 500-650 ℃ of following precipitation hardening annealing, the hardness of object reaches the hardness value that is higher than 65HRC like this.
6. according to the method for claim 5, molten metal is limited in the following concentration range in weight % for one or more elements and/or element set:
Co 19.0-25.0 is preferably 20.0-23.0
W???????????10.0-25.0
Mo 7.0-18.0 is preferably 8.0-14.0
W+2Mo 22.0-34.0 is preferably 24.0-28.0
C 0.008-0.16 is preferably 0.01-0.14
N 0.02-0.08 is preferably 0.025-0.068
V, Nb, Ti, Zr, Ta (combinations of individual element or these elements)
0.14-0.8, be preferably 0.15-0.5
Be limited to 0.7 on the Al, be limited to 0.5 on preferred
Si 0.12-0.6 is preferably 0.15-0.5
Al+Si 0.12-0.8 is preferably 0.15-0.6
Ni＜0.3, be preferably＜0.2
Mu＜0.3, be preferably＜0.2
Cr＜1.2, be preferably＜0.9
7. according to the method for claim 4 or 5, in the method, molten metal additionally with until the carbon of 1.0 weight % with until the nitrogen of 0.2 weight %, and the component until the total content of 2.45 weight % of the one or combination with the elemental vanadium, niobium, the tantalum that form single carbide and nitride is made alloy, at this, the content of elemental carbon and nitrogen is respectively 0.4-0.46 with the ratio of the element that forms single carbide or nitride, and object passes through intermetallic phase, for example (Fe, Co)
7(W, Mo)
6Precipitation and harden by the carbide of fine dispersion and/or so sedimentary overlapping covering of nitride or special nitride.
8. according to the method for claim 4-6, in the method, before the metal-powder jet by nitrogen with the hot isostatic pressing method compacting, in powder, add one or more and have powder particle size until 5 μ m, total amount hard material powder until 28 volume %, and in metal-powder homogeneous distribution.
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| CN104708005A (en) * | 2013-12-12 | 2015-06-17 | 百乐特殊钢有限两合公司 | Method for the manufacture of objects from iron-cobalt-molybdenum/tungsten-nitrogen alloys |
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| CN111793773A (en) * | 2019-08-09 | 2020-10-20 | 中南大学 | High-speed steel through Laves phase and mu phase composite strong hardening and preparation method thereof |
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