CN101421425A - Method of pretreatment for quenching of martensitic tool steel and method of quenching - Google Patents
Method of pretreatment for quenching of martensitic tool steel and method of quenching Download PDFInfo
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- CN101421425A CN101421425A CNA2007800132672A CN200780013267A CN101421425A CN 101421425 A CN101421425 A CN 101421425A CN A2007800132672 A CNA2007800132672 A CN A2007800132672A CN 200780013267 A CN200780013267 A CN 200780013267A CN 101421425 A CN101421425 A CN 101421425A
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- C—CHEMISTRY; METALLURGY
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
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Abstract
A method of the pretreatment for quenching of a martensitic tool steel. The method prevents a metal structure from suffering particle inclusion through quenching and can further improve toughness. Also provided is a method of quenching. The method of the pretreatment for quenching of a martensitic tool steel comprises: (a) a stage in which the martensitic tool steel is heated from room temperature to a temperature in the range of from the transformation point A3 to 'the transformation point A3+150 DEG C' and is held at that temperature to cause austenitic transformation; and (b) a stage in which the martensitic tool steel, subsequently to the stage (a), is cooled to a temperature in the range of 'the perlite nose temperature +-100 DEG C' and is held at that temperature to cause perlitic transformation. The method of quenching a martensitic tool steel comprises subjecting a work to the quenching pretreatment, subsequently heating it to the transformation point A3 or higher, holding it at that temperature, and then cooling it.
Description
Technical field
The present invention relates to the quenching pre-treating process and the quenching process of martensitic tool steel.
Background technology
As the heat treating method that the toughness of the tool steel that makes by quenching the martensitic that metal structure is adjusted into single-phase or two phase constitutions of " martensite+bainite " of martensite improves, adjust the motion that speed of cooling when quenching forms to the metal structure of expectation and be suggested in a large number.
For example, open in the flat 9-182948 communique (patent documentation 1) spy from real desire applicant's motion, as the quenching method that makes the refrigerating work procedure multistage in order to improve toughness, proposition is heated to quenching temperature and keeps (Fig. 2: (6), (7)), in refrigerating work procedure with different speed of cooling carry out the method for multistage cooling (Fig. 2: (8A), (8B)) thereafter.In addition, the real desire applicant opens flat 11-310821 communique (patent documentation 2) the spy, the spy opens in the flat 11-350034 communique (patent documentation 3) and also proposes, and improves the flexible quenching method by making the refrigerating work procedure multistage.
Patent documentation 1: the spy opens flat 9-182948 communique
Patent documentation 2: the spy opens flat 11-310821 communique
Patent documentation 3: the spy opens flat 11-350034 communique
Described spy opens that flat 9-182948 communique, spy are opened flat 11-310821 communique, the spy opens the disclosed quenching method of flat 11-350034 communique, and what say is the growth that is suppressed at the bainite structure that generates in the process of cooling of quenching, thereby toughness is improved.
Yet, situation about confirming when the present inventor studies is, even use the multistage cooling, if observe the grain size number after quenching, still unusual thickization of Bu Fen crystal grain then, observe thick generally grain and fine grain mutually miscellaneous be called as a metal structure that mixes.
Summary of the invention
So, the objective of the invention is to, the mixed granulation in a kind of metal structure after can preventing to quench is provided, further make the quenching pre-treating process and the quenching process of the martensitic tool steel that toughness improves.
The present inventor is with by quenching, and it is object that metal structure is adjusted into martensite martensitic tool steels single-phase or two phase constitutions of " martensite+bainite ", and the method that toughness is improved is studied with keen determination.
At first, the refrigerating work procedure during for the quenching always carried out has carried out various researchs, has difficulties but more positively prevent to mix grain.Therefore, find when attempting carrying out various research, before quenching during the specific heating curve figure of employing, can make metal structure homogeneous after the quenching and fine, thereby reach the present invention for the heating curve figure before quenching.
So, according to first viewpoint of the present invention, provide the quenching pre-treating process of martensitic tool steel shown below.
Be a kind of quenching pre-treating process that comprises as the martensitic tool steel of next stage:
(a) martensitic tool steel is heated to the temperature range of A3 transformation temperature～" A3 transformation temperature+150 ℃ " from room temperature, keeps and make stage of its austenite phase transformation in this temperature;
(b) follow the described stage (a), described martensitic tool steel is cooled to the temperature range of " perlite nose temperature ± 100 ℃ ", make the stage of its pearlitic transformation in this temperature maintenance.
According to this embodiment of the quenching pre-treating process of this martensitic tool steel, preferably at described stage (a), the heating-up time of the A1 transformation temperature of the temperature that begins from room temperature to austenite phase transformation is no more than 1 hour.
According to another embodiment of the quenching pre-treating process of described martensitic tool steel, preferred martensitic tool steel, in quality % contain C:0.10～2.0%, below the Si:2.0%, Mn; Below 2.0%, Cr:1.0～15.0%, Mo:10.0% is following and below Ni:4.0%, below the V:4.0%, below the W:20.0% and at least a kind of element selecting the group who constitutes below the Co:10.0%.
According to another other embodiments of the quenching pre-treating process of described martensitic tool steel, preferably this quenching process is applied to the metal die that formed by martensitic tool steel.
According to second viewpoint of the present invention, provide a kind of quenching process of martensitic tool steel shown below.
Be a kind of quenching process of martensitic tool steel:
(a) martensitic tool steel is heated to the temperature range of A3 transformation temperature～" A3 transformation temperature+150 ℃ " from room temperature, keeps making the stage of its austenite phase transformation in this temperature;
(b) follow the described stage (a), described martensitic tool steel is cooled to the temperature range of " perlite nose temperature ± 100 ℃ ", keep the stage that makes its pearlitic transformation and be cooled to room temperature in this temperature;
(c) the described martensite tool steel of refrigerative is heated to temperature more than the A3 transformation temperature, after this temperature keeps, implements quench treatment.
According to the 3rd viewpoint of the present invention, provide the quenching process of martensitic tool steel shown below.
Be a kind of quenching process that comprises as the martensitic tool steel of next stage:
(a) martensitic tool steel is heated to the temperature range of A3 transformation temperature～" A3 transformation temperature+150 ℃ " from room temperature, keeps making the stage of its austenite phase transformation in this temperature;
(b) follow the described stage (a), described martensitic tool steel is cooled to the temperature range of " perlite nose temperature ± 100 ℃ ", keep making the stage of its pearlitic transformation in this temperature;
(c) follow the described stage (b), described martensitic tool steel is heated to temperature more than the A3 transformation temperature, after this keeps, implement the stage of quench treatment.
Under described first and second viewpoints, according to an embodiment of the quenching process of martensitic tool steel, preferably at described stage (a), the heating-up time of the A1 transformation temperature of the temperature that begins from room temperature to austenite phase transformation is no more than 1 hour.
Under described first and second viewpoints, another embodiment according to the quenching process of described martensitic tool steel, preferred martensitic tool steel, in quality % contain C:0.10～2.0%, below the Si:2.0%, below the Mn:2.0%, Cr:1.0～15.0%, below the Mo:10.0% and below Ni:4.0%, below the V:4.0%, below the W:20.0% and at least a kind of element selecting the group who constitutes below the Co:10.0%.
Under described first and second viewpoints, according to another other embodiments of the quenching process of described martensitic tool steel, preferably this quenching process is applied to the metal die that formed by martensitic tool steel.
According to the quenching pre-treating process and the quenching process of martensitic tool steel of the present invention, can suppress thickization and the mixed granulation of the crystal grain that causes because of quenching, can give martensitic tool steel with high tenacity.In addition,, can also reach, can access martensitic tool steel with high tenacity than No. 6 thinner particulates in the grain size number numbering.Should the metal die of this method, can suppress the generation of big crackle etc., compare with carrying out existing quench treatment, can play the life-span and improve such effect.
Description of drawings
Figure 1A represents the hot heating curve figure of first embodiment of the present invention.
Figure 1B represents the hot heating curve figure of second embodiment of the present invention.
Fig. 2 represents the example based on the heating curve figure of existing method.
Fig. 3 represents the metalloscope photo of the tempering material that the present invention obtains.
Embodiment
The maximum of the inventive method is characterised in that, makes the metal structure generation pearlitic transformation this point of martensitic tool steel before quenching.
In existing quenching method, the processed material of instrument steel before quenching can be warming up to following for example 600～800 ℃ of A1 transformation temperature, attempting to eliminate the surface and the inner temperature difference of processed material, and is once remaining on this temperature.Then, be heated to the above suitable temperature of A3 transformation temperature, kept with quenching temperature., adjust speed of cooling cool off, to obtain improving the effectively metal structure of expectation of toughness thereafter.
In this existing method, the metal structure when keeping with quenching temperature is because of there is the coarse-grained situation that becomes in austenitic growth.Be considered to as its reason, because the influence of hot-work that processed material tool steel is implemented before quenching and annealing etc. causes the metal structure of the processed material tool steel before quenching to become mixed grain.
If become coarse grain under quenching temperature, even then adjust speed of cooling in the cooling engineering, not only " bainite+martensite " tissue still becomes mixed grain easily, and is difficult to fine.
On the other hand, in the present invention, must condition to make metal structure that being treated to of pearlitic transformation taken place before quenching quickly.Adopt the heating curve figure of Figure 1A, Figure 1B that a concrete example of the present invention is described with regard to JIS SKD61.
Figure 1A, Figure 1B are the examples of representational heating curve figure of the present invention.Figure 1A is the processing to the last stage of quenching, and the operation (Figure 1A: (1), (2), (3), (4), (5)) of the tool steel intermediate wood before then obtaining quenching is the heating curve figure of (Figure 1A: (6), (7), (8)) of quenching.In addition, Figure 1B is in the operation that makes it to take place pearlitic transformation (Figure 1B: (5)) afterwards, through refrigerating work procedure (Figure 1B: (9)), and the example of the representational heating curve figure when having obtained taking place the tool steel intermediate wood of quenching usefulness of pearlitic transformation.
In any method, all be by temperature range that martensitic tool steel is heated to " A3 transformation temperature～A3 transformation temperature+150 ℃ " and the operation (Figure 1A, Figure 1B (3), (4)) that is kept, and make metal structure generation austenite phase transformation.
Also have, also can carry out the tool steel intermediate wood of resulting quenching usefulness among Figure 1B is heated to more than the A3 transformation temperature once again, and the quenching that is kept.
In the present invention, be heated to the temperature range of A3 transformation temperature～" A3 transformation temperature+150 ℃ ", and the purpose that remains on the operation of this temperature is that it is to handle for the pearlitic transformation by subsequent handling, and fine perlite is formed at austenitic crystal boundary and intracrystalline.
At this moment, when the temperature of austenite phase transformation (Figure 1A, Figure 1B: (4)) was too high, austenite crystal was grown up, and when ensuing perlite, can not form fine perlite at the austenite crystal intragranular, but remaining as austenite under the state of not phase transformation.As a result of be, when being warming up to quenching temperature, remaining austenite crystal becomes to look thick, and the crystal grain diameter after the quenching is thick, and having becomes the possibility of mixing grain, so the temperature of the temperature of austenite phase transformation and pearlitic transformation is very important.
Therefore in the present invention, the temperature (Figure 1A, Figure 1B: (4)) of austenite phase transformation is decided to be the temperature range of A3 transformation temperature～" A3 transformation temperature+150 ℃ ", is heated to synthermal and keeps.Its reason be because, under the temperature that is lower than the A3 transformation temperature, can not get austenite structure, surpassing the temperature field of " A3 transformation temperature+150 ℃ " in addition, then austenite crystal might become to look thick.The preferred temperature of austenite phase transformation is the temperature range of A3 transformation temperature～" A3 transformation temperature+50 ℃ ".
Also have, at this moment, though processed material keeps with the temperature of regulation, the preferred hold-time serves as abundant to arrive after the temperature of stipulating 0.5 hour～2 hours.
In addition, at this moment, when confirming whether processed material arrives the temperature of regulation, can make it directly to contact processed material surface and measure with armoured thermocouple.
Secondly in the present invention, be cooled to the temperature field of " perlite nose temperature ± 100 ℃ ", carry out the processing (Figure 1A, Figure 1B: (5)) of pearlitic transformation at the temperature field of " perlite nose temperature ± 100 ℃ ".
By this processing, perlite is formed at austenite grain boundary and intracrystalline, and apparent crystal grain is by miniaturization.In order to obtain this effect people, the temperature field that is adjusted to " perlite nose temperature ± 100 ℃ " is very important.If in the high temperature territory that exceeds 100 ℃ of perlite nose temperature, if be cooled to the low temperature region that exceeds 100 ℃ of perlite nose temperature, then be difficult to obtain the micronized effect of apparent metal structure, because of the austenite structure former state that phase transformation not is remaining remaining, quenching heating thereafter keeps in the operation, and crystal grain might become to look thick.
Yet, confirm directly that in the operation of reality whether fully being phase-changed into pearlitic structure has any problem, therefore, make the isothermal phase change curve with test film in advance, be effective with decision in the hold-time of the temperature field of " perlite nose temperature ± 100 ℃ ".
Also have, preferred temperature field is the temperature field from perlite nose temperature to " 100 ℃ of perlite nose temperature negative (-) ", by keeping at the low temperature side lower than perlite nose temperature, can expect effect of the present invention more.
Metal structure after actual pearlitic transformation is handled, what for example have in JIS specification SKD61 is characterized as, at austenite grain boundary, intracrystalline, form the different metal structure of form of pearlitic structure, the feature that has in JIS SKD11 is, at austenite grain boundary, intracrystalline, become the metal structure of homogeneous.
The influence of hot-work and annealing etc. before quenching, forms pearlitic operation by using, owing to can access the 2nd effect that the conversion metal structure becomes the 1st effect of the essential factor of mixing grain and is adjusted into fine pearlitic structure based on of the present invention.
Continue quenching pre-treating process of the present invention, processed material is heated to more than the A3 transformation temperature, keep, then cool off quenching, thereby can access martensitic tool steel through quench treatment with this temperature.
Quenching can be used following operation shown in Figure 1A: after the processing (Figure 1A: (5)) of pearlitic transformation, be heated to the above and maintenance (Figure 1A: (6) of A3 transformation temperature, (7)), then cool off (Figure 1A (8)), quench with member to quenching, also can be shown in Fig. 1 (b), handle (Figure 1B: (5)) afterwards at pearlitic transformation, cool off (Figure 1B: (9)), once cooling off and behind the tool steel intermediate wood as quenching usefulness, the tool steel intermediate wood of quenching usefulness is heated to temperature more than the A3 transformation temperature once again, after this temperature maintenance, quench, perhaps also can implement the multistage refrigerative from the temperature more than the described A3 transformation temperature and quench as shown in Figure 2.
If consider productivity, then shown in Figure 1A, after pearlitic transformation is handled, be heated to the above temperature of A3 transformation temperature, remain in this temperature after, cool off and become the tool steel intermediate wood, it is favourable then to quench.
But, no matter select which kind of method, all to become fine pearlitic structure in advance, be warming up to quenching temperature, under this temperature, keep, at this moment because the austenite product nucleus can increase, so austenite crystal also can be fine and becomes the size of homogeneous, by to its cooling, the martensitic stucture that the obtains fine and homogeneous that also becomes.Thus, can improve toughness.
Also have, the speed of cooling of quenching is carried out as common quenching, and carry out chilling with the fast speed of cooling of separating out than troostite (troostite) or grain boundary carbide of speed of cooling and get final product, also can be multistage cools off.
In addition, in the present invention, in the heating process that is warmed up to the temperature of austenite phase transformation (Figure 1A, Figure 1B: (4)) (Figure 1A, Figure 1B: (1), (2), (3)), the heating-up time that is warming up to the A3 transformation temperature from the A1 transformation temperature is particularly preferably in 1 hour.
The A1 transformation temperature is the temperature that a part of austenite structure phase transformation begins, and the A3 transformation temperature is the temperature that all becomes austenite structure.If the heating-up time is slow excessively, then crystal grain becomes to look thick easily, is in 1 hour therefore.Be preferably in 30 minutes.
Also have, processed material is heated from the surface, and inner specific surface heats slowly.If inner and surperficial heat-up rate difference, the deviation of crystal grain then takes place easily on inner and surface, therefore, more preferably make inside and surface all at 1 hour with interior intensification.
Therefore, in the heating process that is warmed up to the temperature of austenite phase transformation (Figure 1A, Figure 1B: (4)) (Figure 1A, Figure 1B (1), (2), (3)), once carrying out temperature in the temperature range of " negative 200 ℃ of A1 transformation temperature～A1 transformation temperature " and keeping (Figure 1A, Figure 1B: (2)) to get final product.By once keeping, can reduce the internal difference in temperature of processed material, have again, during to the temperature (Figure 1A, Figure 1B: (4)) of austenite phase transformation, can reduce the internal difference in temperature of processed material at heat up (Figure 1A, Figure 1B: (3)).
, so-called martensitic tool steel of the present invention is meant the steel that can be by quenching metal structure be adjusted into single-phase or two phase constitutions of " martensite+bainite " of martensite.These steel are if carry out observation by light microscope after quenching, then in visual field area occupation ratio, surpassing 50% is martensitic stucture.For example comprise JIS SKD61, SKD62, SKT4 etc.
Below, set forth preferred composition about martensitic tool steel of the present invention.Unit all is quality %.
C (carbon): 0.10～2.0%
Making carbon content is that 0.10～2.0% reason is, when the carbon amount was lower than 0.10%, the carbon amount was very few, and carbon can't be diffused into intragranular, does not have carbide to separate out at intragranular, if surpass 2.0%, then the carbide surplus reduces toughness.Preferred C (carbon) is: 0.20～0.60%.
Below the Si:2.0%
Si reductor as when fusion in tool steel adds.But if heavy addition, then toughness reduces.Therefore be below 2.0% in the present invention.Be preferably 0.15～1.20%.
Below the Mn:2.0%
Mn reductor and sweetening agent as when fusion in tool steel adds.But, if then toughness reduction of heavy addition.Therefore, be below 2.0% in the present invention.Be preferably 0.30～1.00%
Cr：1.0～15.0％
Cr makes hardenability improve in tool steel, adds for improving the such purpose of tensile strength and toughness.But if heavy addition, then toughness reduces on the contrary.Therefore be 1.0～15.0% in the present invention.Be preferably 1.0～13.0%.
Below the Mo:10.0%
Mo makes hardenability improve in tool steel.In addition, form fine carbide, add for making high temperature tensile strength increase such purpose by tempering.But if heavy addition, then toughness reduces on the contrary.Therefore be below 10.0% in the present invention.Be preferably 0.20～5.00%.
Add among following Ni, V, W, the Co at least a kind
Ni:4.0% following (removing 0%)
Ni makes hardenability improve in tool steel, is added for improving the such purpose of toughness.But if heavy addition then can reduce transformation temperature, hot strength reduces.Therefore be below 4.00% in the present invention.Be preferably below 2.0%.
V:4.0% following (removing 0%)
V is crystal grain thinning in tool steel, and toughness is improved.In addition, the carbonitride by tempering formation high rigidity is added for the purpose that increases tensile strength.But if heavy addition, then toughness reduces on the contrary.Therefore be below 4.00% in the present invention.Be preferably 0.10～1.10%.
W:20.0% following (removing 0%)
W hardenability in tool steel improves.In addition, form fine carbide, be added for the purpose that increases high temperature tensile strength by tempering.But if heavy addition, then toughness reduces on the contrary.Therefore be below 4.00% in the present invention.Be preferably 0.10～1.10%.
Co:10.0% (removing 0%)
Co increases fervid rigid in tool steel, is added for the purpose that increases high temperature tensile strength.Be below 10.00% in the present invention.
More than, the surplus beyond the element of explanation comes down to Fe.Surplus in the category of Fe, also comprises unavoidable impurities in fact certainly.In addition, for example Nb, Ti are because be to crystal grain miniaturization effective elements, so also can make it to contain in the scope below 0.20% of the degree that can not make the toughness deterioration.
In addition, A1 is an element of accelerating the diffusion of carbon, has the effect of separating out that promotes carbide under pearlitic transformation, therefore also can make it in the scope below 0.20% to contain.
Described the present invention preferably is applied to metal die.
Application the present invention and quenching in recent years, require to improve the life-span of metal die material,, thereby is the method that makes crystal grain miniaturization high tenacityization, if then can satisfy the desired demand characteristics of metal die as one of method of high lifeization.
Also have, when being applied to metal die, the temperature on temperature inside, surface can make the cooling cave directly contact armoured thermocouple and measure.
Embodiment
Illustrate in greater detail invention by following embodiment.
First-selection becomes 6 of the tool steel members of martensitic of the processed material of 15mm T * 15mmW * 50mmL with preparation for experiment.Material is JIS specification SKD61, forms to be presented in the table 1.
Before experiment, use and the test film of the test portion of preparing as same composition, measure A1, A3 transformation temperature, in addition, test film is heated to 900 ℃, make the isothermal phase change curve thereafter, confirm the perlite nose and reach the hold-time that pearlitic transformation finishes.Consequently, the A1 transformation temperature is 823 ℃, and the A3 transformation temperature is 857 ℃, and the perlite nose kept 30 minutes with 750 ℃, and the temperature that pearlitic transformation finishes, finishes thereby confirm pearlitic transformation more than 2 hours with 750 ℃ of maintenances.
[table 1]
(weight %)
| C | Si | MN | Ni | Cr | Mo | V | W | Co | Surplus |
| 0.37 | 0.29 | 0.59 | 0.57 | 5.07 | 1.55 | 0.61 | - | - | Fe and unavoidable impurities |
* annotate) "-" mark represents not have and adds
Following Fig. 1 (a) experimentizes to 6 tool steel members with described composition.
The tool steel member is heated to 790 ℃ (Figure 1A (1)) below the A1 transformation temperature, keep 1 hour (Figure 1A: (2)) after, with the rate of heating heat temperature raising (Figure 1A: (3)) of 40 ℃/h temperature (900 ℃, 1000 ℃) to austenite phase transformation.Because the A1 transformation temperature is 823 ℃, the A3 transformation temperature is 857 ℃, so the heating-up time of the A1 transformation temperature～A3 transformation temperature when being warming up to the temperature of austenite phase transformation is in 1 hour.
Then, after keeping hour with the temperature of austenite phase transformation (Figure 1A: (4)), implement the processing that 700 ℃ * 5h keeps, 750 ℃ * 5h keeps, 800 ℃ * 5h keeps the pearlitic transformation of (Figure 1A: (5)), become the tool steel intermediate wood of quenching usefulness.
Secondly, the tool steel intermediate wood of the above-mentioned quenching usefulness of quenching to 1030 ℃ of specified temperature (Figure 1A: (6)), keeps that (Figure 1A: (7)) cools off (Figure 1A: (8)) after 1 hour with the rate of heating reheat of 40 ℃/h, and the tool steel member obtains quenching., carry out 2 tempering, hardness is adjusted into 43 ± 1HRC, obtain the tempering material thereafter.
Carry out 2U pendulum impact test, metal structure observation, measure grain size number with the tempering material that obtains by these experiments.These results are presented in the table 2.
In addition, the metal structure photo after the quenching-tempering is presented among Fig. 3.Also have, Fig. 3 is the metal structure photo after quenching-tempering of the present invention's example No.6.
[table 2]
As shown in table 2, if use the present invention, the mixed granulation of the metal structure after then can preventing to quench, and the average crystallite grain size number becomes No. 7.5, maximum grain size number number become than No. 7 thin particulates, and toughness is improved.In addition, by the microphotograph of Fig. 3 also as can be known, utilize heat treating method of the present invention, can access the metal structure of fine and homogeneous.
Utilize possibility on the industry
According to the present application, quench, the crystal grain after the tempering becomes fine, therefore can have in the toughness to tool steel in the purposes of requirement and utilize. Be used for the heat treatment of metal die, can high tenacity, thus the effect that life expectancy is improved.
Claims (9)
1. the quenching pre-treating process of a martensitic tool steel wherein, comprises as the next stage:
(a) martensitic tool steel is heated to the temperature range of A3 transformation temperature～" A3 transformation temperature+150 ℃ " from room temperature, keeps making the stage of its austenite phase transformation in this temperature;
(b) follow the described stage (a), described martensitic tool steel is cooled to the temperature range of " perlite nose temperature ± 100 ℃ ", make the stage of its pearlitic transformation in this temperature maintenance.
2. the quenching pre-treating process of martensitic tool steel according to claim 1, wherein, in the described stage (a), the heating-up time of the A1 transformation temperature from room temperature to the temperature that begins as austenite phase transformation is no more than 1 hour.
3. the quenching pre-treating process of martensitic tool steel according to claim 1 and 2, wherein, described martensitic tool steel in quality % contain C:0.10～2.0%, below the Si:2.0%, below the Mn:2.0%, Cr:1.0～15.0%, below the Mo:10.0%, and below Ni:4.0%, below the V:4.0%, below the W:20.0% and at least a kind of element selecting below the Co:10.0%.
4. according to the quenching pre-treating process of each described martensitic tool steel in the claim 1～3, wherein, be applicable to the metal die that forms by martensitic tool steel.
5. the quenching process of a martensitic tool steel wherein, comprising:
(a) martensitic tool steel is heated to the temperature range of A3 transformation temperature～" A3 transformation temperature+150 ℃ " from room temperature, keeps making the stage of its austenite phase transformation in this temperature;
(b) follow the described stage (a), described martensitic tool steel is cooled to the temperature range of " perlite nose temperature ± 100 ℃ ", keep the stage that makes its pearlitic transformation and be cooled to room temperature in this temperature;
(c) the described martensite tool steel of refrigerative is heated to temperature more than the A3 transformation temperature, after this keeps, implements quench treatment.
6. the quenching process of a martensitic tool steel wherein, comprising:
(a) martensitic tool steel is heated to the temperature range of A3 transformation temperature～" A3 transformation temperature+150 ℃ " from room temperature, keeps making the stage of its austenite phase transformation in this temperature;
(b) follow the described stage (a), described martensitic tool steel is cooled to the temperature range of " perlite nose temperature ± 100 ℃ ", keep making the stage of its pearlitic transformation in this temperature;
(c) follow the described stage (b), described martensitic tool steel is heated to temperature more than the A3 transformation temperature, after this keeps, implement the stage of quench treatment.
7. according to the quenching process of claim 5 or 6 described martensitic tool steels, wherein, in the described stage (a), the heating-up time of the A1 transformation temperature from room temperature to the temperature that begins as austenite phase transformation is no more than 1 hour.
8. according to the quenching process of each described martensitic tool steel in the claim 5～7, wherein, described martensitic tool steel in quality % contain C:0.10～2.0%, below the Si:2.0%, below the Mn:2.0%, Cr:1.0～15.0%, below the Mo:10.0%, and below Ni:4.0%, below the V:4.0%, below the W:20.0% and at least a kind of element selecting below the Co:10.0%.
9. according to the quenching process of each described martensitic tool steel in the claim 5～8, wherein, be applicable to the metal die that forms by martensitic tool steel.
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| JP108173/2006 | 2006-04-11 | ||
| JP2006108173 | 2006-04-11 | ||
| PCT/JP2007/057907 WO2007119721A1 (en) | 2006-04-11 | 2007-04-10 | Method of pretreatment for quenching of martensitic tool steel and method of quenching |
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| CN101421425A true CN101421425A (en) | 2009-04-29 |
| CN101421425B CN101421425B (en) | 2011-06-29 |
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| JP (1) | JP5288259B2 (en) |
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| JP3544131B2 (en) * | 1999-01-14 | 2004-07-21 | 株式会社日本製鋼所 | Manufacturing method of medium carbon steel |
| JP3556139B2 (en) * | 1999-11-18 | 2004-08-18 | 株式会社神戸製鋼所 | Wear-resistant cast steel and method for producing the same |
| JP2001294935A (en) * | 2000-04-06 | 2001-10-26 | Sanyo Special Steel Co Ltd | Method for producing tool steel excellent in toughness |
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2007
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Also Published As
| Publication number | Publication date |
|---|---|
| JP5288259B2 (en) | 2013-09-11 |
| WO2007119721A1 (en) | 2007-10-25 |
| CN101421425B (en) | 2011-06-29 |
| JPWO2007119721A1 (en) | 2009-08-27 |
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