CN85102029A - Forgeability in nickel superalloys improves - Google Patents
Forgeability in nickel superalloys improves Download PDFInfo
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- CN85102029A CN85102029A CN85102029.1A CN85102029A CN85102029A CN 85102029 A CN85102029 A CN 85102029A CN 85102029 A CN85102029 A CN 85102029A CN 85102029 A CN85102029 A CN 85102029A
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Abstract
Narrated the method that improves the cast superalloy forging property.By dissolving this material and, causing that very thick γ ' precipitates mutually, to form a microstructure that surpasses timeliness from slowly cooling off near dissolving line temperature.Then this material can isothermal forging.
Description
The present invention relates to be reinforced the forging under forging, the especially as cast condition of nickel-base high-temperature alloy material of γ ' phase, and specially refer to the thermal treatment that improves these material forging propertys.
Nickel base superalloy is widely used on the gas turbine.A purposes is to do the turbine disk.Along with the comprehensive development of the motor performance performance requriements to turbine disk material improves.Early stage engine is done turbine disk material with the derivation alloy of steel and steel.These materials are replaced by first-generation nickel base superalloy soon, Waspaloy alloy for example, and it can forge, though some difficulty usually.
Nickel base superalloy intensity depends primarily on γ ' phase.The trend of nickel base superalloy development is to improve γ ' phase volume percentage ratio to improve intensity.Contain about 25%(volume with the Waspaloy alloy of engine turbine disk in early days) γ ' phase, and the turbine disk alloy of development contains this phase of about 40-70% recently.The increase of γ ' phase volume percentage ratio has reduced the forging property of alloy.The Waspaloy material can be by the ingot casting blank forging, and the forging that the stronger turbine disk material of newly-developed can not safety, and need to use more expensive powder metallurgy technology production capacity in next life to be machined to the shaping dish base of final size economically.United States Patent (USP) the 3rd, 519, No. 503 and the 4th, 081, a kind of powder metallurgy process of No. 295 narrations successfully is used for producing engine plate basically.It is very successful that this method proof is used the powder metallurgy starting material, is seldom successful with casting raw material still.
United States Patent (USP) the 3rd, 802 No. 938,3,975, No. 219 and 4,110, also relates to the forging of disk material No. 131.
In a word, tend to high-intensity disk material and cause processing difficulties, thereby only the powder metallurgy technology of reliable costliness solves.
The objective of the invention is to narrate a kind of high-strength casting high temperature alloy that makes can easily forged method.
Another object of the present invention is a kind of heat treating method that improves the nickel-base high-temperature alloy material forging property greatly of narration.
A further object of the invention provides a kind of forging γ ' and surpasses the 40%(volume mutually) the method for cast superalloy material, this material is non-fireable with other method.
Further purpose is the combination that discloses a kind of thermal treatment and forging method, and it will produce a kind of microstructure with perfect recrystallization of uniform fine grain size, and will reduce forging stress greatly.
A further object of the invention provides a kind of nickle-based high temperature alloy products of high forging property, and it has the γ ' phase constitution above timeliness, and the mean sizes of γ ' phase is above 3 microns.
The intensity of nickel base superalloy is mainly from the γ ' phase particle that is distributed on the γ ' phase matrix.This is with Ni mutually
3The Al compound is a base, indivedual alloying elements, and for example Ti and Nb can partly replace Al.Refractory element, for example Mc, W, Ta and Nb can strengthen γ ' matrix mutually, and when adding Cr and Co, also can bring elements such as micro-C, B and Zr usually into.
Table 1 has been listed the nominal composition of the various superalloys that use under the hot operation condition.The Waspaloy alloy can be forged by strand usually.Remaining alloy is not by waiting directly consolidation of static pressure thermocompressor (NHIP) usually by powder compacting, is exactly by forging the powder blank of consolidation; Because γ ' phase content height, the strand that forges these composition alloys is normally unpractical, although the Astroloy alloy does not lean on powder technology sometimes by forging.
Be included in the alloy of table 1 and it seems that can utilize the composition scope of other alloy that the present invention processes is (weight percentage) 5～25%Co, 8～20%Cr, 1～6%Al, 1～5%Ti, 0～6%Mo, 0～7%W, 0～5%Ta, 0～5%Nb, 0～5%Re, 0～2%Hf, 0～2%V, all the other are essentially Ni, also have a spot of micro-C, B and Zr simultaneously.The summation of Al and Ti content is generally 4～10%, and the summation of Mo+W+Ta+Nb is generally 2.5～12%.The present invention is widely used for γ ' phase content and reaches the 75%(volume) nickel base superalloy, especially for containing volume greater than 40%(), be more suitable for volume greater than 50%() γ ' phase and by common (non-powder metallurgy) technology be non-fireable alloy.
In cast nickel-base alloy, γ ' exists with two kinds of forms: eutectic and non-eutectic.Eutectic γ ' is formed at process of setting mutually, but not eutectic γ ' is formed by solid precipitation when solidifying postcooling.Eutectic γ ' mainly is present in crystal boundary mutually, and particle size is generally quite big, reaches about 100 microns.The non-eutectic γ ' that plays main strengthening effect in the alloy is present in intragranular mutually, and typical sizes is 0.3～0.5 micron.
Heat the material to high temperature, γ ' phase can enter melt.A temperature that enters melt mutually is its solubility curve temperature.The dissolving of γ ' phase (or precipitation) betides in the temperature range.In this is open, term: " dissolving initial " is used for describing the temperature of observing the dissolving beginning and (measured the temperature of determining by the optics metallographic, from this temperature the 5%(volume is arranged slowly during cool to room temperature) γ ' enter melt mutually), term: " dissolving end lines " is meant the temperature (still being determined by the optics metallographic) that dissolving is finished substantially.With reference to " γ ' phased soln line temperature " even without adjective: low/high, also can understand this and be meant high dissolving line temperature.
Eutectic forms mutually in a different manner with non-eutectic γ ', has different compositions and dissolving line temperature.Low and high non-eutectic γ ' typically dissolves the line temperature mutually and hangs down 28～84 ℃ than eutectic γ ' phased soln line temperature is about.In MERL76 composition alloy, about 1121 ℃ of non-eutectic γ ' phased soln initial temperature, dissolving end lines temperature is about 1196 ℃.Eutectic γ ' phased soln initial temperature is about 1188 ℃, and γ ' phased soln end lines temperature is about 1219 ℃ (because initial melting temperature is about 1196 ℃, not having partial melting eutectic γ ' phase just can not dissolve fully).
Forging is a kind of usually under pressure, and the temperature more than recrystallization temperature makes the method for metal working of flow of metal.Most of forging procesies have three characteristics to method and product requirement.(1) finished product has desirable microstructure, and uniform recrystallized structure is preferably arranged, and the essentially no crackle of (2) product requires relative low stress with (3) method.Certainly, this relative importance of three changes with particular case.
In the topmost content of the present invention, comprise and form a kind of serious overaging (surpassing timeliness) γ ' phase constitution in superalloy.The precipitation strength material, for example the mechanical property of nickel base superalloy changes with the mutually sedimentary size of γ '.The mechanical property peak value obtains when γ ' phase size is about 0.1～0.5 micron.Surpass the timeliness under the particle size condition that peak performance is provided, produce a tissue that is called overaging.Surpassing the timeliness tissue is defined as: 3 times (preferably at least 5 times) of the γ ' phase size when average non-eutectic γ ' phase size is the generation peak performance at least are big (diameter) so.Because have forging property is purpose, so γ ' phase size refers to the size under forging temperature.Thick like this γ ' phase constitution is provided, can improves the forging property of material significantly.Clearly, relevant for the γ ' phase size that improves the forging property needs with γ ' phase per-cent in the material.For the lower material of γ ' phase per-cent, the smaller particles size just can satisfy needed result.For example, we think, to having the 40%(volume) material of γ ' phase content, 1 micron γ ' phase size will be satisfied the demand, and to containing the 70%(volume) 2.5 microns γ ' phase sizes of material require of γ ' phase.
Constant when γ ' phase content, increase with γ ' phase particle size, particle (between the thickness of γ ' phase matrix phase layer) at interval also increases.
According to best mode of the present invention, the casting starting materials is heated to the temperature of (or between dissolving line scope) between the beginning and end temp of γ ' phase.Under this temperature, the non-eutectic γ ' phased soln of part.
According to a slow process of cooling, non-eutectic γ ' will come out with thick form redeposition mutually, and particle size is about 5 or even 10 microns.This thick γ ' phase particle has improved the forging property of material widely.This slowly process of cooling since the thermal treatment temps between two dissolving line temperature, near or finish when being preferably lower than the lower limit dissolving line temperature of non-eutectic γ ' phase, speed of cooling should be less than 5.5 ℃/hour.This method also can be called above ageing treatment.
Fig. 2 has provided the rate of cooling of the RCM82 alloy of listing in the table I and the relation curve between the γ ' phase particle size.As can be seen, cool off slowly more, then γ ' phase particle size is big more.Also there is similar relation curve for other superalloy, but slope of a curve is different with the position, Fig. 3 A, 3B and 3C have provided the RCM82 alloy microscopic structure, and this alloy is cooled to be lower than the temperature (1038 ℃) of γ ' phased soln initial from the temperature (1204 ℃) between eutectic γ ' phased soln line and the non-eutectic γ ' phased soln line with the speed of per hour 1.1 ℃, 2.8 ℃ and 5.5 ℃.The difference of γ ' phase particle size is tangible.Fig. 4 provides the flow stress under special forging process that the RCN82 alloy changes with rate of cooling; Rate of cooling drops to 1.1 ℃/hour from 5.5 ℃/hour, makes required forging flow stress reduce about 20%.Fig. 5 provides on the material of handling according to the present invention and the material according to known art breading, carries out the flow stress and the rheology strain curve of jumping-up forging operation.Common process material static flow stress is about 96.53 MPas, is about at 0.27 o'clock in strain crackle (the high compression ratio is 27%) takes place.The material of handling according to the present invention, passive flow transformation power is about 44.81 MPas, though compression ratio for the 0.9(high compression than 90%), crackle does not take place.
The special benefit of the inventive method is to obtain tiny recrystal grain microstructure uniformly by low relatively deflection.Be upset as under the flat situation at the garden post, produce a compression ratio in height less than about 50% microstructure, and when use usual way with the inventive method, this high compression than need greater than 90%.
Then forge step, forging usually by thermal treatment to produce the maximum machine performance.This processing will comprise solution treatment (being typically in forging temperature or on forging temperature), make to be partly dissolved γ ' phase at least, and then, timeliness makes (tiny) form that dissolved γ ' phase redeposition becomes to need at low temperatures.The people who is proficient in this technology understands that the variation in these steps makes the optimizing of different mechanical propertys become possibility.
Forward another aspect of the present invention now to, starting materials is preferably thin brilliant, is thin brilliant at surf zone at least.All crackles of running at the inventive method duration of test all originate from the surface, and all relevant with the big crystal grain in surface.
We have successfully forged the material that the surface microstructure size is about 1.58～3.18 millimeters (diameters), and little surface crack only arranged.This is to finish by the forging operation of strictness, and cylindrical blank is upset as flat-section.The forging of this form is cylindrical outer surface to be placed have under pulling force condition basic status and free state.The material that has big surface microstructure size (for example 6.35 millimeters) in other not too strict forging also can forge.
We think inner grain-size and in fact can specific surface crystal grain thick greater than about half inch grain-size below cast(ing) surface.Limit grain-size is relevant with chemical ununiformity and segregation, because the segregation effect has produced some very thick crystal grain.Keeping grain-size constant in forging process is no less important.Cause that the processing conditions that crystal grain is significantly grown up is undesirable, reduced forging property because grain-size increases.
Casting starting materials (best) usually carries out hot isostatic pressing (HIP) processing, and this processing is to be enough to place high pressure gas to carry out under the temperature that creep of metals is out of shape to starting materials.Typical condition is pressure 103.4 MPas, and temperature is under γ ' phased soln line, but the reduction of temperature is no more than 84 ℃, and the time is 4 hours.The result who handles makes the internal void and the pore closure of existence.If foundry engieering can guarantee to exempt the pore in the cast article, HIP handles and can not want, if finished product does not require processing, HIP handles and also can not want.
As previously mentioned, γ ' phase size can increase in forging in material.Heat the material to the temperature that a large amount of non-eutectic γ ' phases (promptly at least about 40% volume, preferably at least about 60% volume) enter melt, cooling makes the non-eutectic γ ' of most of dissolved with the big particle redeposition at leisure then.Material is as cold as usually at least and hangs down 28 ℃ than dissolving initial temperature, and great majority are as cold as the temperature near forging temperature usually.
Rate of cooling is less than about 5.5 ℃/hour, preferably less than about 2.8 ℃/hour.With reference to Fig. 1, since 0, arbitrary the straight line of falling between 0 ℃/hour and 5.5 ℃/hour all will produce the result who needs.The fluctuation of the rate of cooling that sembles may not be gratifying.For example see curve 1, it has an A part, in A part rate of cooling above 5.5 ℃/hour.That the chances are is not satisfied for this.We think that present method will allow rate of cooling just over 5.5 ℃/hour, and for example the small portion of process of cooling is 11.1 ℃/hour.But had better not do like this.In the unsettled stove of temperature regulator, carry out process of cooling, can not produce the microstructure that needs, although all rate of cooling are basically less than 5.5 ℃/hour.Certainly, in the stove that has common ON/OFF controller, cool off, will produce a series of very little heat fluctuations, but the thermal inertia of stove has been eliminated these fluctuations.
Further observe, consider curve 2 and 3, these two curves all do not have slope to surpass 5.5 ℃/hour part.Although the both is terminated to the X point, preliminary sign is the result good (slow cooling then soon cold) of result's (relative fast cold joint slow cooling) of curve 3 generations than curve 2 generations.The benefit of Bian Huaing is in fact technical like this, not equal to be economically.
Higher requirement is when carrying out foregoing γ ' when increasing thermal treatment mutually, and grain-size does not increase.A method that prevents grain growth is that material is handled being lower than under the temperature that all γ ' phases all enter melt.By keeping the few but amount (for example 5～30% volumes) of the γ ' phase outside melt that is absolutely necessary, grain growth will slow down.This utilizes the difference of solubleness line temperature between eutectic and the non-eutectic γ ' phase morphology to reach usually.Have in the alloy of high relatively carbon content at some, carbide phase (insoluble basically) is enough to prevent grain growth.If the γ ' that is kept has stable grain boundary mutually, can loosen the temperature limitation that to be supervised when then the present invention being applied to such alloy.Keep γ ' phase also can unite utilization mutually with carbide.Special in not having excessive stretching strain forging process and/or in the forging process of forgeable relatively alloy, a certain amount of grain growth can allow.
Prevent grain growth and keep the enough γ ' phases of material that by using the treatment temp between eutectic and non-eutectic γ ' phased soln line temperature, can be implemented as the eutectic γ ' that the result kept has prevented grain growth mutually.But we know, in some alloys, the solution treatment of alloy may occur, follow redeposition mutually by dissolving earlier eutectic γ ' fully, thereby eliminate eutectic γ ' phase basically.The inventive method still is suitable in this case, only needs to select a treatment temp, keeps few but be absolutely necessary under this temperature, be i.e. an amount that is enough to prevent the γ ' phase of grain growth.
Forging operation is with isothermal ground (using hot-die) and carry out in a vacuum or in inert atmosphere.Here " isothermal " comprises those when forging, the process of temperature variation less (promptly ± 28 ℃), mould temperature be preferably workpiece temperature ± 55 ℃, thereby and anyly can not be enough to make the workpiece Quench to hinder forged mould condition to be only good.Forging temperature is usually less than non-eutectic γ ' phased soln initial temperature, and the reduction of temperature is no more than 110 ℃, although dissolve the lower limit of scope between initial and the end lines temperature at non-eutectic, it also is possible forging.
The following dissolving line of the usually close non-eutectic γ ' phase of forging temperature.Forging is carried out under low strain rate, typically be about 0.1～1 cm// minute.United States Patent (USP) the 4th, 081, No. 295 dual strain rate method can adopt.The forging condition of needs is with alloy, workpiece geometries and forging equipment performance variation, and skilled skilled worker can easily select the condition of needs.
Under normal circumstances, thermal treatment of the present invention allows single job to make and forges the as cast condition nickel-base material to net shape, although geometric condition may require to use different moulds, step (not needing intermediate treatment) is repeatedly forged in use.An operation comprises uses shallow forging die that foundry goods is upset as flat-section, then reaches complicated net shape with pattern.
Under special circumstances, operation of the present invention can repeat, and promptly repeatedly carry out thermal treatment of the present invention except that forging operation, but this is normally unwanted.
Other characteristics and advantage are obviously found out from specification sheets, claim with from accompanying drawing, accompanying drawing diagram one embodiment of the present of invention.
Fig. 1 is a graphic representation, illustrates the variation in the process of cooling;
Fig. 2 provides rate of cooling and the γ ' relation curve of particle size mutually;
Fig. 3 A, 3B, 3C are the micro-metallographs of refrigerative material under the different rates;
Fig. 4 provides rate of cooling and forges the relation curve of flow stress;
Fig. 5 provides when forging with material common and method processing of the present invention, the relation curve of stress and strain;
Fig. 6 A and 6B forge forward and backward Photomicrograph with the material that usual way is handled;
Fig. 7 A and 7B forge forward and backward Photomicrograph with the material that the inventive method is handled.Implement most preferred embodiment of the present invention
A kind of alloy with RCM82 alloy nominal composition in the table 1 is cast into 15.24 centimetres of diameters, high 20.32 centimetres right cylinder, its grain-size is 0.125～0.18 millimeter of an ASTM2-3(mean diameter).This material contains about 60～65%(volume) γ ' phase.Non-eutectic γ ' phased soln line temperature range is about 1121 ℃～1196 ℃, and eutectic γ ' phased soln line temperature range is about 1177～1216 ℃.This foundry goods is produced by specialty metal company, has obviously used United States Patent (USP) the 4th, 261, No. 412.
Foundry goods is handled (1185 ℃, 103.4 MPas, 3 hours) with closed remaining pore (having enough γ ' phase particles to prevent grain growth at 1185 ℃) through HIP.Then 1185 ℃ heat treating castings, the time is 2 hours, is cooled to 1093 ℃ (crystal grain does not take place grows up again) with 1.1 ℃ of/hour speed.Result's non-eutectic γ ' phase particle size is about 8.5 microns.Be this material 76% with 0.1 cm// minute be swaged to compression ratio under 1121 ℃ then, the flat-section that forms 30.48 centimetres of high 5.0 cm x diameters does not have crackle.
Under the situation without heat treating method of the present invention, this draught can have big crackle, and the forging force that needs is greater than using the used forging force of the inventive method.Even in the place that does not have crackle, it is organized also is undesirable, wherein its part recrystallize only.
The characteristics of some microstructures are illustrated by Fig. 6 A, 6B, 7A and 7B.Fig. 6 A is the microstructure of cast material.This material does not carry out thermal treatment of the present invention.What seen by Fig. 6 A is the crystal boundary that contains a large amount of eutectic γ ' phases.Can see that at the center of crystal grain size is less than about 0.5 micron tiny γ ' phase particle.
Fig. 6 B is the microstructure that usual way is forged the back material.What seen by Fig. 6 B is tiny recrystal grain on former crystal boundary, and the material that its surrounds does not have recrystallize basically.This uneven (chain) microstructure can not provide best mechanical property.
The tissue of the same alloy after heat-treating by the present invention before Fig. 7 A provides and forges.See at former crystal boundary and to contain eutectic γ ' region.And importantly be crystal grain inside contain size than Fig. 6 A in the corresponding much bigger γ ' phase particle of particle size.γ ' phase particle size is about 8.5 microns in Fig. 7 A.In Fig. 7 B, forging the back microstructure is recrystallize and uniform basically.Fig. 7 B material is considered to have than the superior mechanical property of Fig. 6 B material.
In a word, can reach three purposes for using the inventive method to forge, and the deterioration of quality does not take place with the non-fireable material of other method.Significantly increase the compression ratio (Fig. 5) when crackle takes place; Finished product has the microstructure (Fig. 7 B) of improvement; Forge the flow stress that needs and reduce (Fig. 4) widely.
Certainly the invention is not restricted to special embodiment given here and narration, under the spirit and new ideas scope situation that do not have to break away from by following claim explanation, can make different variations and modification.
Claims (26)
1, a kind of method that improves nickel base superalloy product forging property is characterized in that it comprises:
This product of thermal treatment is so that make a large amount of γ ' phased solns, slowly cool off this product to the temperature below the γ ' phased soln initial temperature to produce a kind of γ ' phase constitution of thick overaging.
According to the method for claim 1, it is characterized in that 2, rate of cooling is less than about 5.5 ℃/hour.
According to the method for claim 1, it is characterized in that 3, rate of cooling is less than about 2.8 ℃/hour.
According to the method for claim 1, it is characterized in that 4, this product is cooled to be lower than at least γ ' and begins about 28 ℃ of temperature mutually.
According to the method for claim 1, it is characterized in that 5, this product is cooled to be lower than at least γ ' and begins about 55 ℃ of temperature mutually.
According to the method for claim 1, it is characterized in that 6, this product is cooled at least about as intending the low temperature of forging temperature.
7, according to the method for claim 1, it is characterized in that, keep enough γ ' phases not dissolve to prevent that crystal grain from significantly growing up.
8, according to the method for claim 1, it is characterized in that, intend existing under the forged temperature at least about the 40%(volume) non-eutectic γ ' mutually dissolved.
9, a kind of method that increases average γ ' phase particle size in nickel base superalloy under forging temperature is characterized in that it comprises:
This product of thermal treatment slowly cools off this product to the temperature that is lower than r ' phased soln initial temperature so that make a large amount of γ ' phased solns, to produce a kind of γ ' phase constitution of thick overaging.
10, method according to Claim 8 is characterized in that, rate of cooling is less than about 5.5 ℃/hour.
11, method according to Claim 8 is characterized in that, this product is cooled to be lower than at least γ ' and begins the about 28 ℃ temperature of temperature mutually.
12, method according to Claim 8 is characterized in that, this product is cooled at least about as intending the low temperature of forging temperature.
13, method according to Claim 8 is characterized in that, keeps enough γ ' phases not dissolve to prevent that crystal grain from significantly growing up.
14, method according to Claim 8 is characterized in that, intend existing under the forged temperature at least about the 40%(volume) non-eutectic γ ' mutually dissolved.
15, a kind of forgeable nickel base superalloy product is characterized in that, average γ ' phase particle size is greater than about 2.5 microns under forging temperature.
According to the product of claim 15, it is characterized in that 16, average γ ' phase particle size is above 5 microns.
17, a kind of its hot hardness at high temperature is corresponding to γ ' phase particle size, locate to present the Inco nickel based high-temperature alloy product of a peak value in a specific granule size (peak value particle size), it is characterized in that, this product is having an average γ ' phase particle size under typical forging temperature, it at least 3 times to the peak value particle size.
18, according to the product of claim 17, it is characterized in that having at least 5 times of average γ ' phase particle sizes to the peak value particle size.
19, forge the method for nickel base superalloy product, it is characterized in that, comprise the following steps.
A. this product of thermal treatment is so that dissolve a large amount of γ ' phases, and at leisure this product is cooled to be lower than γ ' phased soln initial temperature to produce the γ ' phase constitution of a thick overaging;
B. with hot-die this product of isothermal forging under the temperature that is lower than non-eutectic γ ' phased soln initial temperature.
According to the method for claim 19, it is characterized in that 20, rate of cooling is less than about 5.5 ℃/hour.
According to the method for claim 17, it is characterized in that 21, this product is cooled to be lower than at least γ ' and begins about 28 ℃ of temperature mutually.
According to the method for claim 17, it is characterized in that 22, this product is cooled at least about as intending the low temperature of forging temperature.
23, according to the method for claim 17, it is characterized in that, keep enough γ ' phases not dissolve, significantly grow up to prevent crystal grain.
24, according to the method for claim 17, it is characterized in that, intend that forged temperature exists at least about the 40%(volume) non-eutectic γ ' mutually dissolved.
25, a kind of method of forging the cast nickel-base alloy product, this alloy contains the volume greater than 40%() γ ' phase, it is characterized in that, comprise the following steps.
A. this product of hot isostatic pressing is with closed internal porosity;
B. this product of thermal treatment so that be dissolved in is intended the volume of 40%(at least that exists under the forging temperature) non-eutectic γ ' phase, and keep enough γ ' to prevent grain growth, to cool off this product at leisure less than about 5.5 ℃/hour speed to approximating the temperature of intending forging temperature, to produce the γ ' phase constitution of an overaging;
C. with hot-forging die this product of isothermal forging under the temperature that is lower than non-eutectic γ ' phased soln initial temperature.
According to the method for claim 19, it is characterized in that 26, the difference of forging temperature and non-eutectic γ ' phased soln initial temperature is less than 111 ℃, forge speed be about 0.05～2/ cm// minute.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
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| CN 85102029 CN1012182B (en) | 1983-12-27 | 1985-04-01 | Improved forgeability in nickel superalloys |
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| US06/565,490 US4574015A (en) | 1983-12-27 | 1983-12-27 | Nickle base superalloy articles and method for making |
| CN 85102029 CN1012182B (en) | 1983-12-27 | 1985-04-01 | Improved forgeability in nickel superalloys |
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| CN85102029A true CN85102029A (en) | 1987-01-17 |
| CN1012182B CN1012182B (en) | 1991-03-27 |
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| EP1428897A1 (en) * | 2002-12-10 | 2004-06-16 | Siemens Aktiengesellschaft | Process for producing an alloy component with improved weldability and/or mechanical workability |
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