CN103814145A - Method for producing high speed steel - Google Patents
Method for producing high speed steel Download PDFInfo
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- CN103814145A CN103814145A CN201280045555.7A CN201280045555A CN103814145A CN 103814145 A CN103814145 A CN 103814145A CN 201280045555 A CN201280045555 A CN 201280045555A CN 103814145 A CN103814145 A CN 103814145A
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/02—Making ferrous alloys by powder metallurgy
- C22C33/0257—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/12—Both compacting and sintering
- B22F3/14—Both compacting and sintering simultaneously
- B22F3/15—Hot isostatic pressing
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/02—Making ferrous alloys by powder metallurgy
- C22C33/0257—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements
- C22C33/0278—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5%
- C22C33/0285—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5% with Cr, Co, or Ni having a minimum content higher than 5%
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/36—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.7% by weight of carbon
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Abstract
A method for producing a high speed steel that with reference to its chemical composition consists of the following elements: 1-3 wt-% carbon (C), 3-6 wt-% chromium (Cr), 0-7 wt-% molybdenum (Mo), 0-15 wt-% tungsten (W), 3-14 wt-% vanadium (V), 0-10 wt-% cobalt (Co), 0-3 wt-% niobium (Nb),0-0.5 wt-% nitrogen (N), 0.2-1 wt-% yttrium (Y), and remainder iron (Fe) and unavoidable impurities, and wherein Mo+0.5W = 2-10 weight%, characterised in that the method comprises the steps of: providing a powder comprising the elements of said high speed steel, forming a body of said powder, and subjecting said body to elevated heat and pressure such that a consolidation of the powder thereof is achieved.
Description
Technical field
The present invention relates to a kind of method for the manufacture of rapid steel, described rapid steel has according to the composition of claim 1 preamble.
Background technology
Need to be applicable to now the type material of the application that relates to high temperature and wearing and tearing.These Application Areass for example can comprise heat forged instrument, the internal combustion engine component etc. for metal forming.
There are several different specific alloys that are suitable for high-temperature use, for example FeCrAl alloy, NiCrAl alloy, Ni base alloy, Co base alloy and special stainless steel.But FeCrAl alloy, NiCrAl alloy and Ni alloy are too soft so that can not be used for above-mentioned Application Areas.Some Co base alloys are the hard still too expensive practical alternatives that consequently can not serve as major applications enough.
Rapid steel (HSS) at room temperature provides good hardness and still can maintain hardness at up to 600 ℃.But, for some application, be desirably in and at the temperature that is significantly higher than 600 ℃, still maintain room temperature hardness.
In the art, known rapid steel and cobalt-base alloy meeting are improved to the hardness under higher temperature.
In this area, there are several different modes of improving the operability of rapid steel in high temperature application.
Be known in the art, add for example cobalt of alloying element (Co), with the strong carbide forming element combination of working by base matter (base mass) or matrix, thereby can increase rapid steel hardness at high temperature and increase wear resistance.
Also known in the art, owing to forming carbide based on described alloying element, therefore adding alloying element for example tungsten, molybdenum and vanadium the ability that can increase rapid steel withstand high temperatures, i.e. its hot hardness and high temperature abrasion resistance.
Also known in the art, the increase of the amount by the carbide that forms with carbide forming element for example chromium, molybdenum, tungsten and vanadium alloying, can contribute to the wear resistance of rapid steel energetically.
A large amount of alloying elements make rapid steel be difficult to manufacture by the foundry engieering of standard.The microtexture of gained has the problem that is caused serious segregation by very coarse carbide, and it causes rapid steel to have extreme difference toughness and intensity.In application, wherein after by steel casting, described steel is forged, due to the impact of this deformation on material microstructure, therefore overcome some in these problems.
For the alloy that also needs to tolerate oxidation/corrosive atmosphere except high temperature and wearing and tearing, due to synergy, some new demands are therefore also produced.For be exposed to corrosion/oxidation and lost material simultaneously, material behavior is definitely important.Oxidation kinetics and oxide skin mechanical properties and binding property become the important factor about alloy purposes.
By specific coatings is deposited on rapid steel, can change its oxidation characteristic (uses ion beam assisted depositing and implanted ions to reduce the wearing and tearing in key engine assembly, the people such as J.H.Arps, Surface and Coatings Technology(surface and coating technology) 841996, the 579-583 pages).But the use of such coating in the application of serious wear is restricted, because it only produces thin protective coating (in micrometer range) to steel.Can expect in the application of wearing and tearing within the scope of millimeter, because primary coat will wear away, so the steel work with such coating is by further coating follow-up needs.This will significantly increase the cost of product in the predicted life of product.
Another feasible solution will be the surface modification of utilizing rapid steel, for example implanted ions (ion beam modification of Ion beam modification of metals(metal), G.Dearnley, nuclear instrument and the method for Nuclear Instruments and Methods in Physics Research(in physics research) B501990,358-367 page).But the problem of implanted ions is the Gaussian distribution of ion, it causes the material characteristics with change in depth.Implanted ions also means that the used thickness of modified layer is restricted; Therefore it is not suitable in above-mentioned application.
The people's such as Isamoto United States Patent (USP) 5989491 discloses a kind of method that uses the dispersion-strengthened sintered alloy of oxide compound.The contriver of this part patent points out, in the dispersion-strengthened hot resistant powder metallurgical alloy of oxide compound, the fine dispersion of oxide particle, except the intrinsic basic thermotolerance of refractory alloy, also can strengthen creep-rupture strength.But disclosed alloy is not suitable for the machine applications that relates to for example aforementioned wearing and tearing of wearing and tearing in US5989491, because the impact of the interpolation of the not oxidated thing fine particle of the wear resistance of the finished product.
Several patents disclose rare earth element with the rapid steel of high temperature association in purposes, for example, referring to JP1142055A, JP63213641A, CN101037760A, JP1159349A, JP1142056A, CN101078090A, JP6299298A, CN1693527A, JP57143468A, JP2005281839A, CN101831590A, JP8041592A, JP57143471A, JP2003253396A and JP1008252A.But with standard foundry engieering in the situation that, the manufacture of all these alloys is all reluctant.The degree of some alloyings in these rapid steel is demonstrated, may cause following problem: alloying element segregation during fixed (solidification), and form coarse carbide structure.Therefore, manufacturing the microtexture that has the rapid steel of high-content alloying element and rare earth element and realize uniform material character simultaneously and fully control, is reluctant.
JP57085952A(summary) alloy of composition corresponding to the composition of the claims in the present invention 1 preamble disclosed.Must think that discussed document also discloses casting as the method for manufacturing described alloy.Must think that wherein disclosed steel has following microtexture, it causes material have bad intensity and therefore make it not too be suitable as wear parts.
Goal of the invention
The object of the invention is to propose a kind of method that reduces or solve the problems referred to above relevant to manufacturing rapid steel, described rapid steel comprises rare earth element yttrium (Y) for relating to the application of high temperature wear.
The present invention also aims to provide a kind of manufacture method of the ability that improves the wearing and tearing of rapid steel withstand high temperatures.
Therefore, the present invention is based on the thinking to following problem: to casting and add yttrium to segregation relevant in conventional rapid steel and coarse carbide structure.
Summary of the invention
Method by following manufacture rapid steel reaches object of the present invention, described rapid steel is following elementary composition by % by weight about its chemical constitution: carbon (C) 1-3, chromium (Cr) 3-6, molybdenum (Mo) 0-7, tungsten (W) 0-15, vanadium (V) 3-14, cobalt (Co) 0-10, niobium (Nb) 0-3, nitrogen (N) 0-0.5, yttrium (Y) 0.2-1, surplus is made up of iron (Fe) and inevitable impurity, and wherein Mo+0.5W=2-10, described method is characterised in that and said method comprising the steps of: the powder that the element that comprises described rapid steel is provided, form the base substrate of described powder, and make described base substrate stand high heat (temperature) and high pressure, to realize the fixed of its powder.This step can be called to consolidation step or hot isostatic pressing (HIP) step.
During described consolidation step, steel is in solid-state, i.e. non-melt state.Preferably, temperature during described high-temperature step is within the scope of 950-1200 ℃, wherein and the alloying element such as content low alloy of Mo, W, Co, Y etc. relatively high for C content, may need lesser temps, and the wherein high alloy of content relatively low for C content and described other alloying element, needs the comparatively high temps in described scope.If temperature is too low, net result will be porous material so, and if excess Temperature, so described material may start fusing, and this should be avoided.
Pressure during consolidation step depends on temperature, and temperature is to select for every kind of independent steel composition.Can be by means of the relatively low temperature of elevated pressures compensation.Preferably, for composition within the scope of the present invention, defined in claim 1 and dependent claims, and for mentioned consolidation step temperature range, pressure should be in 800-1500 clings to scope.Conventionally,, for concrete selected temperature, the alloying element of high level is by pressure higher needs.
In whole specification sheets, mention that " embodiment " or " a kind of embodiment " refer to special characteristic, structure or the characteristic of an associated description of embodiment to be included at least one embodiment of disclosed theme.Therefore, in whole specification sheets, occur that phrase " in one embodiment " or " embodiment " may not refer to same embodiment everywhere.In addition, special characteristic, structure or characteristic can combinations in any suitable manner in one or more embodiments.
According to an embodiment, then make now to have very low porousness level or stand soft annealing without the base substrate of porous consolidated powder at all.Carrying out soft annealing is for the ease of follow-up alloy processing.Preferably, the top temperature of soft annealing step is the temperature of aforementioned consolidation step, and minimum temperature to be steel experience softening and steel in carbide spheroidization and martensitic transformation to the residing temperature of ferrite.Under any circumstance, temperature must not be so high so that its cause the serious alligatoring of Carbide size.
Selected soft annealing temperature will depend on alloy composition.Conventionally, the alloying element of high level is by annealing temperature higher needs.Therefore, for composition within the scope of the present invention, soft annealing temperature will be preferably at 600 ℃ within the scope of 900 ℃.The time length of soft annealing answers sufficiently long to reach sufficiently high ferrite content in material.Preferably, after soft annealing, ferritic-austenitic ratio should be at least 95/5.Steel is cooling relatively lentamente, in order to avoid form martensite or bainite in alloy.Preferably, depend on alloy composition, rate of cooling is within the scope of 5-20 ℃/h.Be cooled to following temperature with this speed, at the temperature lower than this temperature, rate of cooling will no longer affect bainite, martensitic formation.Lower than described temperature in the situation that, cooling can be naturally cooling, and rate of cooling can only depend on reigning external conditions.For alloy within the scope of the present invention, this temperature can be within the scope of 600-700 ℃.
After this, if desired can process base substrate, and after this depend on the concrete composition of the steel of sclerosis, at the temperature within the scope of 950-1200 ℃, heat-treat by sclerosis (austenitizing) step.After sclerosis, in steel, will there be some residual austenites, the major portion of steel is now martensite.Remove this austenite by means of follow-up annealing steps.During first step, retained austenite is converted into martensite.But this martensite is very frangible, this by another annealing steps of needs to become enough extending.Depend on the austenitic composition and the amount that after sclerosis, remain in steel, the number of times of annealing steps and time length can change.According to an embodiment of the invention, carry out annealing steps until the content of retained austenite is 5% to the maximum, is preferably 2% to the maximum.
As the technique effect of disclosed the inventive method or is below, rare earth element yttrium is evenly distributed in powder above.If the rapid steel of design makes by routine casting method according to the present invention, high reactivity Yt is by segregation and can not be uniformly distributed so.Yttrium being uniformly distributed in high speed steel substrate-matrix can cause producing following oxide skin, and described oxide skin is configured as and effectively adheres to rapid steel.Add yttrium also change oxide skin growth kinetics so that skin Fast Growth to saturation thickness.At this, more than saturation thickness, the growth velocity of oxide skin significantly reduces.Due to yttrium fine dispersion in high speed steel substrate-matrix, therefore the useful technique effect of wear resistance under high temperature is made us to against expectation good.This technique effect has exceeded those of ordinary skills to using powder metallurgy process to add the desired effect of yttrium.In fact, make us against expectation, the raising of technique effect is large like this, so that has compensated and used powder metallurgy as the relevant higher cost of the method for manufacturing this steel, makes described steel be highly suitable for wherein making in its any application that stands heavy wear condition.Especially, the average Carbide size of steel is by much smaller the average Carbide size of the respective material than using casting to manufacture.According to the present invention, described steel should have the average Carbide size of <3 μ m, and this will have when the inventive method is manufactured for it.Due to manufacture method of the present invention, therefore described steel also will have isotropic microtexture, and this is also conducive to its wear resistance.In other words, the present invention has instructed and should carry out consolidation step and follow-up heat treatment step, so that described steel obtains average Carbide size and the isotropic microtexture of <3 μ m.
Except high temperature and wearing and tearing also comprise in the application of oxidation/corrosion, the character of the oxide skin forming is extremely important.In oxidation/corrosion applications, the Fast Growth by oxide skin self carries out repairing and having very important significance fast to the damage in oxide skin, and the material that this can the manufacture of the application of the invention method is realized.
According to the inventive method embodiment, provide powdered mixture to comprise the step that the deposite metal that comprises described element argon gas is atomized into described powder.By using the argon gas atomization of deposite metal, compared with using nitrogen atomization, the amount of nitride minimizes, and wherein uses nitrogen can cause that nitride forms.
According to the present invention, the yttrium content of described rapid steel is within the scope of 0.20 % by weight to 1.0 % by weight.Preferably, the yttrium content of described rapid steel is greater than 0.40 % by weight, and is less than 0.70 % by weight, is more preferably less than 0.60 % by weight.In a preferred implementation, described yttrium content within the scope of 0.45-0.60 % by weight, for example 0.4-0.5 % by weight, for example 0.4,0.41,0.42,0.43,0.44,0.45,0.46,0.47,0.48,0.50 % by weight.
The yttrium content limiting in above interval produces above-mentioned active effect to described oxide skin.Particularly the yttrium content within the scope of 0.45-0.60 % by weight has very well improved the ability of described rapid steel withstand high temperatures wearing and tearing.The lower limit in described interval 0.20% defines the starting point that can determine from it the remarkable active effect of yttrium to high temperature abrasion resistance.The described upper limit 1% has shown to determine from it interval terminal of the remarkable active effect of yttrium to high temperature abrasion resistance.
According to the inventive method embodiment, carbon (C) content of described rapid steel is within the scope of 1.1-1.4 % by weight.The amount of carbon should be enough to form the necessary carbide of wear resistance of described rapid steel.Preferably, described carbon amount should be enough to manufacture the rapid steel with enough hardenabilitys.Lower limit 1.1% defines and forms the minimum carbon content with the carbide of expectation and the rapid steel of hardenability.The greatest carbon content that the upper limit 1.4% defines in this embodiment, can form austenite higher than it.
According to the inventive method embodiment, described chromium (Cr) content is within the scope of 3.0-6.0 % by weight.This good hardenability of interval generation and essential carbide form.But too much chromium causes that the risk that forms residual austenite and overtempering increases; Therefore must not exceed the upper limit of Cr.According to an embodiment, described Cr content is within the scope of 4.0-5.0 % by weight.
According to the inventive method embodiment, described molybdenum (Mo) content is within the scope of 4.5-5.5 % by weight.This interval is by making the meeting raising hot hardness of rapid steel and the carbide precipitation of wear resistance cause secondary hardening.
According to the inventive method embodiment, described tungsten (W) content is within the scope of 6.0-7.0 % by weight.This interval is by making the meeting raising hot hardness of rapid steel and the carbide precipitation of wear resistance cause secondary hardening.
The known fact is that this steel is had to similar effect for Mo and W and therefore it can be replaced to a great extent each other.According to claim 1, Mo+0.5W=2-10 % by weight.According to a preferred implementation, Mo+0.5W=5-8.5 % by weight.Should point out, the element with lower limit 0 % by weight is optional.
According to the inventive method embodiment, described vanadium (V) content is within the scope of 3.0-5.0 % by weight.This interval is by making the meeting raising hot hardness of rapid steel and the carbide precipitation of wear resistance cause secondary hardening.But too much vanadium can cause rapid steel to become frangible, and therefore must not exceed the upper limit.According to a preferred implementation, described V content is within the scope of 3.0-3.5 % by weight.
According to the inventive method embodiment, cobalt (Co) content of described rapid steel is within the scope of 8.0-9.0 % by weight.Rapid steel and cobalt-base alloy meeting are improved to tempering resistance and hot hardness, and tempering resistance and hot hardness are for having very important significance for the high speed steel capital of high temperature wear application.Described cobalt amount is also by making retained austenite easily change into the amount of martensite retained austenite to affect during tempering, thereby affects the hardness of described rapid steel.The selected interval of cobalt is the interval that is suitable for the rapid steel of this composition, and wherein high-content is more that economy is traded off and non-science restriction.Alternatively, if use cobalt in the scope not limiting above, cobalt contents is 0% or in impurity level so.
Even if the p/m high speed steel of manufacturing by the inventive method also has such as the extraordinary character of high temperature wear resistant in oxidation/corrosive atmosphere.
Accompanying drawing explanation
Now Reference numeral associated with accompanying drawing and chart use is further explained to design of the present invention, wherein
Fig. 1 is the schematic diagram of " pin-dish (pin on disc) " testing installation,
Fig. 2 illustrates the cross section perpendicular to longitudinal typical groove of evaluating available from " pin-dish ",
Fig. 3 is illustrated in " pin-dish " experiment, for alloy A, B and C, and the chart of the groove depth at room temperature and 650 ℃,
Fig. 4 is illustrated in " pin-dish " experiment, for alloy A, B and C, and the chart of the VOLUME LOSS of every meter at 650 ℃, and
Fig. 5 illustrates the HRC hardness of alloy A, B and C.
Embodiment
The industry manufacture of work in-process, assembly and cutter based on p/m high speed steel started from before 35 years.The hot isostatic pressing (HIP) of the manufacture of powder metallurgy first of rapid steel based on atomized powder and fixed.The heat forged of hot isostatic pressing blank normally after HIP step.This manufacture method is still the main powder metallurgy process of manufacturing rapid steel.
The initial object of the research and development of the powder metallurgy processed to rapid steel is to improve its functional property and performance in required application.The main advantage of powder metallurgy manufacturing process is without segregation and equal even isotropic microtextures.Therefore in p/m high speed steel, avoided the known problem of coarse and serious carbide segregation in conventional cast steel and forged steel.
Therefore, the powder metallurgy manufacture method with the rapid steel of q.s carbon and carbide forming element makes carbide discrete distribution, and it has solved the low strength relevant to the rapid steel of routine manufacture and the problem of low toughness to a great extent.
Therefore, the present invention relates to a kind of method of manufacturing rapid steel.The step providing by following elementary composition powder is provided the inventive method: the vanadium (V) of the molybdenum (Mo) of the carbon (C) of 1-3 % by weight, the chromium (Cr) of 3-6 % by weight, 0-7 % by weight, the tungsten (W) of 0-15 % by weight, 3-14 % by weight, the cobalt (Co) of 0-10 % by weight, the niobium (Nb) of 0-3 % by weight, the nitrogen (N) of 0-0.5 % by weight, the yttrium (Y) of 0.2-1 % by weight, surplus is iron (Fe) and inevitable impurity, wherein Mo+0.5W=2-10 % by weight.Should point out, the element with lower limit 0 % by weight is optional.
In an embodiment of the inventive method, described in provide powdered mixture to comprise the step that the deposite metal that comprises described element argon gas is atomized into described powder.In a preferred embodiment of the present invention, the atomization of fusing rapid steel argon gas causes that forming overall dimension is the rapid steel particle of 160 μ m.
After described powder is provided, from described powder forming base substrate.This shaping for example can comprise described powder is poured in cryptomere device.Then cryptomere device is vacuumized, for example by make its stand 24 hours lower than the negative pressure of 0.004 millibar so that described cryptomere device is vacuumized.Then cryptomere device is sealed to maintain the described negative pressure in cryptomere device.By making cryptomere device stand long-time section of for example high temperature for example approximately 1150 ℃ and for example approximately 1000 bar of high pressure of 2 hours, realize the fixed of described powder.This last consolidation step is called to hot isostatic pressing, HIP.
After HIP step, be soft annealing step, preferably, at 900 ℃, carry out soft annealing step, then under the rate of cooling of 10 ℃/h, cool the temperature to 700 ℃, allow thus base substrate to naturally cool to room temperature.
After soft annealing, can carry out mechanical workout and (austenitizing) step of preferably hardening at 1100 ℃ to base substrate, and at 560 ℃, carry out three follow-up annealing steps, each lasting 60 minutes, naturally cool to room temperature therebetween.
The material obtaining from these subsequent steps shows extraordinary homogeneity and without above-mentioned segregation and coarse carbide structure, and most important effect is yttrium to be evenly distributed in the matrix-matrix of rapid steel.
Table 1
For the superior character of proved inventive method, design the rapid steel that there is no optional elements, referring to table 1.By getting rid of optional elements, clear and proved concisely the high temperature abrasion resistance improving because of described method.The rule of thumb test " pin-dish " of high temperature abrasion resistance is below described.
Table 1 illustrates the element of the rapid steel using in experiment.With the element manufacture melting body in table 1, and make powder from these melting bodies by means of the gas atomization that uses argon gas.The granularity <160 μ m of the alloy B in table 1 and the powder of C, and the granularity <500 μ m of the powder of alloy A.
In the following description, for further example the present invention in detail, the non-limitative experiment of implementing will be described.
With powder filled capsules device, to continue to prepare sample, the spiral welded tube that described cryptomere device is 73mm by diameter is made.Then cryptomere device is exposed to lower than lower 24 hours of the pressure of 0.004 millibar; Then cryptomere device is sealed to maintain described pressure.
For the powder in fixed cryptomere device, under 1150 ℃ and 1000 bar, carry out the hot isostatic pressing operation of 2 hours.Then make sample at 900 ℃, stand soft annealing step, then under the rate of cooling of 10 ℃/h, cool the temperature to 700 ℃, allow thus sample to naturally cool to room temperature.
Then sample carried out to mechanical workout and heat-treat by sclerosis (austenitizing) step at 1100 ℃, and at 560 ℃, carrying out three follow-up annealing steps, each lasting 60 minutes, naturally cooling to room temperature therebetween.
Final preparation process is included in automatic grinding/polissoir and progressively grinds and polishing sample.During final polishing step, use 1 μ m diamond suspensoid.
Fig. 1 illustrates the short form test equipment for Tribological Test; That this equipment is known in the art and be referred to as " pin-dish ".The principle of " pin-dish " Tribological Test is as follows; Make sample 1 rotate many turning around axle 5 with speed omega.With the rotation of sample 1 side by side, power F is put on to pin 2, pin 2 then same power F is put on to ball 3.Ball 3 is by Al
2o
3make and diameter is 6mm.Power F on the rotation of sample 1 and ball 3 causes forming groove 6 in sample 1.
In order to evaluate wearing character under high temperature, the bottom of " pin-dish " equipment is contained in stove 4.Therefore, stove 4 can be heated to the bottom of sample 1, ball 3 and pin 2 operating temperature of expecting.
Fig. 2 illustrates the cross section perpendicular to longitudinal groove 6 of groove 6.The tolerance that is used as sample wear resistance to the depth d of groove 6 bottoms will be measured from the polished surface of sample.Another figure of wear resistance is cross-sectional area 7, be defined as groove 6 lower than sample 1 polished surface perpendicular to the longitudinal cross-sectional area of groove 6.Use profile and the depth d of Veeco Wyko NT9100 white light interferometer estimation groove 6.
Manufacture according to above-described series of samples and according to " pin-dish " step of above-outlined and test." pin-dish " result is presented in Fig. 3, and the linear velocity in this test is 20cm/ second, and the power F applying is respectively 5N and 20N, and rotary sample 20000 is turned.
As shown in Figure 3, add yttrium reduces groove depth at 650 ℃; The groove depth d that the groove depth d that equals 5.7 μ m, alloy B referring to the groove depth d of alloy A equals 1.9 μ m and alloy C equals 3.7 μ m.This shows, the alloy of manufacturing by the inventive method has at high temperature been realized the wear resistance that expection increases.Compared with rapid steel (alloy A) without yttrium, add 0.5% yttrium (alloy B) to rapid steel and make groove depth d be decreased to approximately 1/3.In addition, adding 1% yttrium (alloy C) to rapid steel reduces groove depth d at 650 ℃.
More representative wear resistance tolerance is the VOLUME LOSS (mm of every meter
3/ m).By the cross-sectional area 7 on track is longitudinal is carried out to integration and the girth divided by groove, calculate the VOLUME LOSS of every meter.In Fig. 4, provide the VOLUME LOSS of every meter; The VOLUME LOSS of alloy A is 4.6 × 10
-5mm
3the VOLUME LOSS of/m, alloy B is 1.8 × 10
-5and the VOLUME LOSS of final alloy C is 4 × 10
-5mm
3/ m.Relation between the yttrium content of rapid steel shown in Fig. 4 and its VOLUME LOSS of every meter.Can clearly draw according to Fig. 4,0.5% yttrium content causes the VOLUME LOSS of every meter minimum.Yttrium content higher than 1% also has beneficial effect to the VOLUME LOSS of every meter.According to this relation, yttrium content 0.5% causes the implicit excellent in abrasion resistance of rapid steel and improves.Although it should be noted that and do not provide in the drawings embodiment D and E, also illustrate because adding to this respective active effect that yttrium produces.
According to the present invention, the yttrium content of described rapid steel is in the scope of 0.2 % by weight to 1 % by weight.Preferably, the yttrium content of described rapid steel is greater than 0.4 % by weight and is less than 0.7 % by weight, be more preferably less than 0.6 % by weight, more preferably 0.4 % by weight to 0.6 % by weight, for example 0.4 % by weight to 0.5 % by weight, for example 0.4,0.41,0.42,0.43,0.44,0.45,0.46,0.47,0.48,0.49 and 0.5.
In Fig. 5, provide sample hardness.The hardness of alloy A is that the hardness of 63HRC, alloy B is that the hardness of 57HRC and alloy C is 56HRC.The conclusion obtaining from Fig. 5 is to add yttrium and can make hardness reduce.Not wishing in situation bound to any specific theory, is that carbon available in the alloy that contains yttrium is less, thereby has reduced hardness to this possible explanation reducing.This has illustrated in the at room temperature main theory by Hardness of High Speed Steel control of Fig. 3 high speed steel wear rate.At room temperature, wear rate improves along with lower hardness.For example, but at high temperature, other mechanism control wearing and tearing, the growth kinetics of oxide skin and mechanical properties.
Claims (15)
1. manufacture a method for rapid steel, described rapid steel is following elementary composition by % by weight about its chemical constitution:
Surplus is iron (Fe) and inevitable impurity, wherein Mo+0.5W=2-10 % by weight,
It is characterized in that said method comprising the steps of:
-powder of the described element that comprises described rapid steel is provided,
-form the base substrate of described powder, and
-make described base substrate stand Gao Re and high pressure to realize the fixed of its powder.
2. the method for manufacture rapid steel according to claim 1, is characterized in that providing described powdered mixture to comprise the step that the deposite metal that comprises described element argon gas is atomized into described powder.
3. the method for manufacture rapid steel according to claim 1 and 2, is characterized in that yttrium (Y) content of described rapid steel is greater than 0.4 % by weight.
4. according to the method for the manufacture rapid steel described in any one in claims 1 to 3, it is characterized in that yttrium (Y) content of described rapid steel is 0.7 % by weight or lower.
5. according to the method for the manufacture rapid steel described in any one in claim 1 to 4, it is characterized in that yttrium (Y) content of described rapid steel is within the scope of 0.45-0.60 % by weight.
6. according to the method for the manufacture rapid steel described in any one in claim 1 to 5, it is characterized in that carbon (C) content of described rapid steel is within the scope of 1.1-1.4 % by weight.
7. according to the method for the manufacture rapid steel described in any one in claim 1 to 6, it is characterized in that chromium (Cr) content of described rapid steel is within the scope of 3.0-6.0 % by weight.
8. according to the method for the manufacture rapid steel described in any one in claim 1 to 7, it is characterized in that chromium (Cr) content of described rapid steel is within the scope of 4.0-5.0 % by weight.
9. according to the method for the manufacture rapid steel described in any one in claim 1 to 7, it is characterized in that molybdenum (Mo) content of described rapid steel is within the scope of 4.5-5.5 % by weight.
10. according to the method for the manufacture rapid steel described in any one in claim 1 to 9, it is characterized in that tungsten (W) content of described rapid steel is within the scope of 6-7 % by weight.
11. according to the method for the manufacture rapid steel described in any one in claim 1 to 10, it is characterized in that Mo+0.5W=5.0-8.5 % by weight.
12. according to the method for the manufacture rapid steel described in any one in claim 1 to 11, it is characterized in that vanadium (V) content of described rapid steel is within the scope of 3.0-5.0 % by weight.
13. according to the method for the manufacture rapid steel described in any one in claim 1 to 12, it is characterized in that cobalt (Co) content of described rapid steel is within the scope of 8.0-9.0 % by weight.
14. 1 kinds are passed through the rapid steel obtaining according to the method described in any one in claim 1 to 13, it is characterized in that the average Carbide size <3 of described rapid steel μ m.
15. rapid steel according to claim 14, is characterized in that described rapid steel has isotropic microtexture.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| EP11181771.4 | 2011-09-19 | ||
| EP11181771A EP2570507A1 (en) | 2011-09-19 | 2011-09-19 | A method for producing high speed steel |
| PCT/EP2012/068428 WO2013041558A1 (en) | 2011-09-19 | 2012-09-19 | A method for producing high speed steel |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN103814145A true CN103814145A (en) | 2014-05-21 |
Family
ID=46852027
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201280045555.7A Pending CN103814145A (en) | 2011-09-19 | 2012-09-19 | Method for producing high speed steel |
Country Status (5)
| Country | Link |
|---|---|
| US (1) | US20140356218A1 (en) |
| EP (2) | EP2570507A1 (en) |
| JP (1) | JP2014530294A (en) |
| CN (1) | CN103814145A (en) |
| WO (1) | WO2013041558A1 (en) |
Cited By (3)
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|---|---|---|---|---|
| CN104128600A (en) * | 2014-07-09 | 2014-11-05 | 浙江工业大学 | Special powder for laser combination manufacturing of hot working die and manufacturing process thereof |
| CN105568152A (en) * | 2015-12-28 | 2016-05-11 | 珠海格力节能环保制冷技术研究中心有限公司 | Alloy powder, alloy raw material composition, alloy part, forming method of alloy part, vane and roller compressor |
| CN108060361A (en) * | 2017-11-09 | 2018-05-22 | 佛山峰合精密喷射成形科技有限公司 | A kind of substitution steel grade of cobalt-containing high speed steel |
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| DE102015213706A1 (en) * | 2015-07-21 | 2017-01-26 | Mahle International Gmbh | Tribological system comprising a valve seat ring and a valve |
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| JP7348415B2 (en) * | 2020-12-28 | 2023-09-20 | 三菱重工エンジン＆ターボチャージャ株式会社 | Nozzle parts, variable nozzle mechanism of variable displacement turbocharger, variable displacement turbocharger and method for manufacturing nozzle parts |
| CN113714497B (en) * | 2021-08-04 | 2023-06-06 | 湖南工业大学 | Gradient powder metallurgy high-speed steel pretreatment powder and treatment method thereof and gradient powder metallurgy high-speed steel preparation method |
| CN114574774B (en) * | 2022-01-19 | 2023-04-07 | 长沙市萨普新材料有限公司 | Stainless powder metallurgy high-speed steel for wet-type rotary die cutting knife roller and preparation method thereof |
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| CN108060361A (en) * | 2017-11-09 | 2018-05-22 | 佛山峰合精密喷射成形科技有限公司 | A kind of substitution steel grade of cobalt-containing high speed steel |
Also Published As
| Publication number | Publication date |
|---|---|
| EP2570507A1 (en) | 2013-03-20 |
| WO2013041558A1 (en) | 2013-03-28 |
| JP2014530294A (en) | 2014-11-17 |
| US20140356218A1 (en) | 2014-12-04 |
| EP2758558A1 (en) | 2014-07-30 |
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