CN107075624A - The application of steel and this kind of steel with high wearability, hardness, corrosion resistance and low heat conductivity - Google Patents
The application of steel and this kind of steel with high wearability, hardness, corrosion resistance and low heat conductivity Download PDFInfo
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- CN107075624A CN107075624A CN201580046492.0A CN201580046492A CN107075624A CN 107075624 A CN107075624 A CN 107075624A CN 201580046492 A CN201580046492 A CN 201580046492A CN 107075624 A CN107075624 A CN 107075624A
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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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
- C21D1/32—Soft annealing, e.g. spheroidising
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C29/00—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides
- C22C29/005—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides comprising a particular metallic binder
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C29/00—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides
- C22C29/02—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides
- C22C29/06—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides based on carbides, but not containing other metal compounds
- C22C29/10—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides based on carbides, but not containing other metal compounds based on titanium carbide
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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
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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
- 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%
- C22C33/0292—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 more than 5% preformed carbides, nitrides or borides
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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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
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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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
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Abstract
The present invention relates to a kind of steel for being used to require the application of high-wearing feature, high rigidity, good corrosion resistance and/or low heat conductivity that can on an industrial scale operate and reliably manufacture.There is at least 56HRC hardness in the state of hardening according to the steel of the present invention.To achieve it, there is at least 30 weight % hardening phase altogether in the institutional framework of steel, the hardening is made up of in addition to TiC particles other carbonized particles, oxidation particle or nitridation particle.The content of TiC particles is at least 20 weight % in the steel according to the present invention.Harden phase particle at this to be embedded into matrix, the matrix is made up of (in terms of weight %) 9.0 15.0% Cr, 5.0 9.0% Mo, 3.0 7.0% Ni, 6.0 11.0% Co, 0.3 1.5% Cu, 0.1 2.0% Ti, 0.1 2.0% Al, remaining iron and inevitable impurity.Its combinations of features makes to be applied to manufacture part, the particularly cutting knife or orifice plate needed for the production and circulation in plastics according to the steel of the present invention.
Description
Technical field
It is used to require answering for high-wearing feature, high rigidity, good corrosion resistance and/or low heat conductivity the present invention relates to a kind of
Steel.
Background technology
If the content explanation of steel alloy given below, as long as no specified otherwise, then these contents explanation refers to respectively
Weight.
Steel with above-mentioned characteristic be particularly suitable for manufacture cutting tool, orifice plate, filter screen, in plastics processing industry
Needed for mechanical mould and like.
Here, typical application field is the reproduction or the machinery of circulation for plastic product, these plastic products are
Backed into fabrication cycles and be fused into melt.In order to which by melt composition granular materials, the melt extrusion passes through one
Orifice plate, melt is with multiple wall scrollsForm extruded from orifice plate.These single lines solidify and then borrowed
Cutting knife that is suitable, being rotated close to orifice plate is helped to cut into single particle.
For accelerated solidification process, plastic melt is implemented under water by the extruding and cutting of orifice plate.The process is in modeling
It is referred to as " underwater cutpellet (Unterwassergranulieren) " in material industry.
For the cutting of plastics cutting knife and for be molded treat the orifice plate of plastic strip that is cut by cutting knife due to they
Residing corrosive environment when using and must have good corrosion resistance and be subjected to the abrasion of grinding herein.For " hole
For the application of plate ", the thermal conductivity that the steel of orifice plate is respectively prepared should be simultaneously relatively low, thus without the modeling for making to contact with each orifice plate
Material melt loses excessive heat and causes the too fast solidification of melt, and too fast solidification can cause the blocking of plate hole.It is this to want
Ask and particularly proposed when orifice plate is so-called " microwell plate " with the bore dia less than 1mm.
The known steel set for the purpose is with (the AISI- titles of material label 1.2379：D2 it is) and known.Its except
Outside iron and inevitable impurity also contain (with weight %'s) 1.55% C, 12.00% Cr, 0.80% Mo and
0.90% V.
Another same steel pandemic in plastics cycle art is with (the AISI- titles of material label 1.3343：M2)
And standardize.It is in addition to iron and inevitable impurity also containing the 0.85-0.9% C (with weight %'s), 0.25%
Mn, 4.1% Cr, 5.0% Mo, 1.9% V and 6.4% W.
With (the AISI- titles of material label 1.4110：440A) normalized martensite steel should be resistant to highest wear requirements,
It is in addition to iron and inevitable impurity also containing the 0.6-0.75% C (with weight %'s), the Mn of maximum 1%, maximum
1% Si, the P of maximum 0.04%, S, 16-18% of maximum 0.03% Cr and maximum 0.75% Mo.The steel is appropriate
Heat treatment after reach minimum 60HRC hardness.
With steel known to trade name " iron-titanium Nikro 128 (Ferro-Titanit Nikro 128) " except iron and can not
Also contain (with weight %'s) 13.5% Cr, 9% Co, 4% Ni and 5% Mo outside the impurity avoided, the steel is special
Door is used to manufacture the component used in the plastic processing of abrasion.Titanium carbide contains in the institutional framework of the steel so constituted
Measure as 30 weight %, this corresponds to TiC about 40 volume % bulk specific gravities.
The steel of known powder metallurgically manufacturing passes through the annealing and subsequent quenching of two to four hours under 850 DEG C of vacuum
About 53HRC annealing hardness is reached after (wherein exposed to the nitrogen atmosphere of the pressure with 1-4.5 bars), the annealing hardness can
To increase to about 62HRC highest hardness by subsequent cure process (wherein steel is shelved six to eight hours at 480 DEG C).By
The steel generally manufactures orifice plate, particle cutting knife, injection-moulding nozzle and screw rod, ring and other plastics for being used to be machined with abrasive action
Operated pressing tool, and the part for pump, filling head and cutting ring, these parts need be used for can filling machine (referring to
“Ferro-Titanit-Die " the numbers of Ferro-Titanit Nikro 128 " included in aus Krefeld " handbooks
According to table, published by Deutsche Edelstahlwerke GmbH).
Horst Hill " need anti abrasive work in order to improve use time in its paper in polymer processing industry
Novel metal matrix composite (MMC) (Neuartige Metallmatrixverbundwerkstoffe (MMC) zur of toolverschleiβbeanspruchter Werkzeuge in der
Polymerverarbeitenden Industrie) " (the great university paper of ripple in 2011, be published in material technology teaching and research room from
In Publication, ISBN 978-3-943063-08-0) in finally propose a kind of steel, it is by (with weight %'s's) 13.5%
Cr, 1.0% Mo, 9.0% Ni, 5.5% Co, 1.0% Cu, 2.0% Ti and 1.25% Al together with remaining iron and
Inevitable impurity composition.TiC contents in the institutional framework of the steel are similarly 30 weight %.But the volume in the institutional framework
Other places is used as hardening phase in the presence of 5 weight % NbC.
The steel so constituted is added in its manufacturing process with laboratory standard for the uncommon of the potentiality full of expectation
Hope.But reliably production in enormous quantities is proved to still suffer from problem its process.
The content of the invention
In this context, it is an object of the invention to provide a kind of steel, its can application conventional method under conditions of with
Industrial standard is produced and with the feature optimized in terms of its characteristic.Same should also propose the practical application of this kind of steel.
In terms of steel, the purpose according to this kind of steel with the feature provided in claim 1 of the invention by obtaining
To realize.
The favourable design of the present invention is provided and equally detailed with the general inventive concept of after image in the dependent claims
Carefully illustrate.
By being used to require high-wearing feature, high rigidity, good corrosion resistance and/or low heat conduction the invention provides a kind of
The steel of the application of property.
According to the present invention steel in the state of hardening have at least 56HRC hardness and in its institutional framework altogether
Containing at least 30 weight % hardening phase, the hardening is in addition to TiC particles also by carbonized particles, oxidation particle or nitridation
Particle is constituted.Here, in the steel according to the present invention, the content of TiC particles is at least 20 weight %.
- according to the present invention, hardening is mutually embedded into matrix, and the matrix is by (in terms of weight %)
9.0-15.0% Cr,
5.0-9.0% Mo
3.0-7.0% Ni,
6.0-11.0% Co,
0.3-1.5% Cu,
0.1-2.0% Ti,
0.1-2.0% Al,
Remaining iron and inevitable impurity composition.
Component according to the steel of the present invention is so adjusted, to cause it to be satisfied with highest demand, such as to adding in plastics
Steel used in work industrial circle and requirement.Correspondingly, manufacture is particularly suitable for use according to the steel of the present invention to use
In the reproduction and the component of circulation of plastic product.Therefore it can such as be manufactured according to the steel of the present invention for making the modeling by wearing and tearing
Expect formed melt composition particle needed for orifice plate, particularly microwell plate, when the hole opening of orifice plate is formed with micron fine degree
To produce during corresponding fine particle, it still has preferable performance.Similarly, can be by the steel according to the present invention
Make the cutting knife for cutting plastic components.This kind of cutting knife, as described above, equally manufactures particle in the plastic strip by melting
During required for, for example by the above-mentioned type orifice plate along granulating direction and produce particle.
In order to be provided as the characteristic needed for this, contain according to the steel of the present invention at least 20 weight %, embedded to body
TiC, the matrix is made contributions by the hardenability separated out to steel while should so select, i.e. independent of each heat
Processing state and ensure the relatively low thermal conductivity less than 35W/mK.
Passive current density according to the steel of the present invention is less than 5 μ A/cm2, in the sulfuric acid of oxygen-free 0.5 molar concentration
In, relative to calomel reference electrode with 600mV/h potential change tachometric survey at 20 DEG C.Therefore exist according to the steel of the present invention
There is corrosion resistance, the corrosion resistance is similar to conventional austenitizing under conditions of higher hardness and the wearability of optimization
The corrosion resistance of stainless steel.
Temperature according to the E modulus determined by ultrasonic measurement according to sound propagation velocity of the steel of the present invention at 20 DEG C
It is more than 270Gpa, particularly greater than 300GPa down, so that according to the steel or the component that is made from it of the present invention also reliably
Meet the peak demand in terms of its intensity.
The thermal coefficient of expansion of steel according to the present invention determined by dilatometer is in 20 DEG C to 600 DEG C of temperature range
7×10-6/ K to 12 × 10-6/ K, application pregnancy of the temperature range for the steel according to the present invention.
By there is extremely hard, the thermodynamically stable TiC particles of sufficient amount, (it has under conditions of relatively low thermal conductivity
Have relatively low density) it is maximized resistance to reference to being obtained according to the steel matrix of the invention set while the thermal conductivity of minimum
Mill property, wherein, the steel matrix equally reaches higher hardness.Therefore, according to the steel of the present invention in an ideal way comprising minimum
20 weight %, accordingly about 30 volume % TiC, or minimum 28 weight %, the TiC for being particularly minimum 30 weight %.But,
The 45 weight % upper limit is not to be exceeded in TiC contents.By this way it is ensured that more process is reliably manufactured and following process
This is according to steel of the invention.Although high hardening phase content causes increased hardness and wearability.But thermal expansion is reduction of, this
Significantly making the composite manufacturing of steel matrix becomes difficult.In addition, higher hardening phase content means that material becomes more crisp and more
It is also easy to produce crackle.Meanwhile, the processing possibility of machinery has been significantly attenuated in the case of too high hardening phase content.Here, pressing
Advantage according to the steel of the present invention is that it can also be processed in the way of conventional cutting.
In addition, hardness and wearability in order to optimize the steel according to the present invention, play facilitation, according to the present invention
Also there are other hardening phases in addition to TiC particles in steel matrix in ground, so that the hardening phase in the institutional framework of steel
Bulk specific gravity is total up at least 30 weight %.This can be in the production process of steel by it is possible to additionally incorporate carbonized particles, nitridation
Grain or oxidation particle and carry out.To this it is alternative or complementally can also according to the present invention defined scope in so adjust
The weight ratio of the element (Ni, Al, Ti) of precipitation is shaped to, it is reliable during the operating procedure that manufacture steel is completed to cause
Ground forms the precipitation for improving hardness of sufficient amount in the base.
Known steel in paper relative to H.Hill already mentioned above, in the steel according to the present invention, Mo and Co
Content substantially increase and Ni and Ti content is substantially reduced.In addition, for according to the present invention alloy Cu, Al, TiC with
And the regulation of NbC contents changes relative to known steel.By adjusting alloy content according to of the invention and reaching, with technique
Large-scale production steel, it has higher hardening compared to weight, and the hardening is mutually embedded in the steel matrix of same high rigidity.By known
Steel concept is set out, and this requires complicated research and experiment, because the effect of each element and phase in referring to the steel of species herein
It is extremely complex with interaction.The steel according to the present invention so obtained is with its high-wearing feature, high rigidity, good corrosion resistant
Corrosion and low heat conductivity have the property combination of optimization.
The precipitation formed in the steel matrix according to the steel of the present invention is intermetallic precipitation, mainly there is element Ni, Al, Ti
It take part in its generation.These elements form Ni3Al and Ni3Ti or mixed form.These intermetallic quantity with 10nm
Level in granular size and be present in institutional framework and be not belonging to always harden phase content.Relative to for example embedded according to this hair
Larger hardening phase particle in the matrix of bright steel, it is intermetallic due to patience of its less size for fretting wear
Bigger effect is not played.But, the intermetallic increase separated out to the hardness and intensity of metallic matrix is played a role simultaneously
Therefore the improvement of performance is equally promoted.
Chromium exists in the steel according to the present invention with 9.0-15.0 weight % content, ensures that required corrosion resistant
Corrosion.For this purpose it is desirable to, Cr contents are 12.5-14.5 weight %.
The molybdenum of the content containing 5.0-9.0 weight % in the steel according to the present invention, so as on the one hand ensure that particularly
The formation of intermetallic phase is on the other hand promoted for enough corrosion resistances of pitting corrosion, is improved by the intermetallic phase
Harden the hardness of the steel matrix embedded by phase.It is desirable that being 6.5-7.5 weight % according to the Mo contents of the steel of the present invention.
The cobalt of the content containing 6.0-11.0 weight % in the steel according to the present invention, so as on the one hand improve martensite
Initial temperature and on the other hand reduce dissolubilities of the Mo in metallic matrix.The steel according to the present invention can be made by this way
Contained Mo more strongly participates in the formation of intermetallic phase in matrix.It is desirable that being 8.0- according to the Co contents of the steel of the present invention
10.0 weight %.
The copper of the content containing 0.3-1.5 weight % in the steel according to the present invention, so as to accelerate precipitation-hardening.It is preferable
, it is 0.5-1.0 weight % according to the Cu contents of the steel of the present invention.
Nickel exists in the steel according to the present invention with 3.0-7.0 weight % content.The nickel of sufficient amount is needed in steel matrix,
So as to make austenite phase stable during the solution annealing implemented at normally about 850 DEG C.This is especially according to the present invention
Material be especially important when being quenched by solution annealing temperature.By the presence of nickel, make austenite stable to this herein
The degree of sample, i.e. martensite is reliably produced in quenching process.If existed in the steel matrix set according to the present invention
Few nickel, then the effect can not be reached with necessary reliability.If there is excessive nickel in steel matrix on the contrary, no
Martensite can be formed, because austenite phase is also stable at room temperature.Second mesh of the nickel in the steel according to the present invention
Be, pass through formed with as Al and Ti intermetallic phase precipitation-hardening.Therefore, in the steel matrix of the steel according to the present invention
In, Ni, Al and Ti content are mutually so coordinated, so as on the one hand realize martensite formation and on the other hand realize precipitation firmly
Change.Preferable mode is, is 4.5-5.5 weight % according to the Ni contents of the steel of the present invention.
Titanium exists in the steel according to the present invention with 0.1-2.0 weight % content, so that it is real to combine Ni as described above
Precipitation-hardening is showed.It is desirable that being 0.8-1.2 weight % according to the Ti contents of the steel of the present invention.
Aluminium also exists in the steel according to the present invention with 0.1-2.0 weight % content, so that with reference to Ni to precipitation-hardening
Play a role.For this it is desirable that being 1.0-1.4 weight % according to the Al content of the steel of the present invention.
It can be hardened according to the steel of the present invention in extremely on-deformable mode, because titanium carbide has relatively low thermal expansion
With without transformation.
The wearability of the steel according to the present invention is improved by adding maximum 4.5 weight % NbC particles.Meanwhile, NbC
Grain has the thermal conductivity lower than TiC, and this plays beneficial effect for the performance of the steel according to the present invention.Except this it
Outside, TiC and NbC are isomorphism carbide and therefore, it is possible to be mutually mixed.This causes mixed carbide during diffusion reaction
Formed.Relative to only be used only TiC, therefore generate valence electron concentration change and thus in the interstitial lattice of carbon formed sky
Position.Also the thermal conductivity according to the steel of the present invention is weakened by this way and improves performance.This effect is particularly worked as
Realized according to when there is at least 2.0 weight % NbC in the steel of the present invention.Here, when NbC contents are 2.0-3.0 weight %
When generate preferable effect.
By the way that the steel according to the present invention is manufactured with powder metallurgy in a conventional manner, it can be ensured that its institutional framework does not have
Segregation and fiber distribution.It is used as carbide particle, nitride particles and the oxide particle of hardening phase in powder according to the present invention
Introduced in metallurgical manufacturing process as " being made " particle.
For powder metallurgically manufacturing, sintering can have both been used to use HIP (high temperature insostatic pressing (HIP)) path.For example,
The super solid phase liquid-phase sintering of comminuted steel shot based on gas atomization is also applied for steel of the production according to the present invention.
In Foller, M.；Meyer,H.；Lammer, A. Wear and Corrosion of Ferro-Titanit
and Competing Materials.In：Tool steels in the next Century:Proceedings of the
5th International Conference on Tooling, September 29-October 1, Leoben, Austria university, 1999
Year, Austria, the 1-12 pages, and in H.Hill, S.Weber, W.Theisen, A.van Benneko's has high-wearing feature
Corrosion-resistant MMC optimization (OptimierungMMC mit hohem
Verschlei β widerstand), in 30.Hagener Symposium, 24.-25.11.2011 or in above-mentioned Horst Hill
Paper in can find generally refer to type here steel powder metallurgically manufacturing during used in operating procedure
Description.
Conventional heat treatment can be carried out in order to adjust its mechanical performance according to the steel of the present invention, wherein, it is heated 2-4
Hour, then quench and then shelved at 480 DEG C 6-8 hours under with the nitrogen atmosphere of the pressure-loaded of 1-4.5 bars.According to
The steel of the present invention generally has the hardness more than 62HRC after such heat treatment.By the heating under vacuum and in inertia
Quenching in atmosphere, it is to avoid the negative effect area in the fringe region of the heat treatment for the semi-finished product being molded respectively by steel
Domain.
If the soft annealing for being defined to pass through 2-4 hours at 850 DEG C will be heat-treated, then have according to the steel of the present invention
There is the hardness more than 50HRC.
Brief description of the drawings
It is then act through embodiment and further illustrates the present invention.Accompanying drawing is shown：
Fig. 1 is a part for the scanning electron micrograph in the section of the sample according to the present invention；
Fig. 2 is a chart, be illustrated therein is according to steel sample produced by the invention and for the steel sample for contrasting and producing
The measurement result of the thermal conductivity of product；
Fig. 3 is a chart, and it is included according to steel sample produced by the invention and for the steel sample for contrasting and producing
The result of the current density-potential measurement of upper implementation；
Fig. 4 is a chart, and it has reproduced the knot of the dilatometer measurement on the sample being made up of the steel according to the present invention
Really.
Embodiment
The characteristic of the steel set to compare according to the present invention, the orifice plate for manufacturing underwater cutpellet or cutting knife with
The characteristic of steel knowing, being set for identical application target, manufactures the steel E and known steel V according to the present invention.Two kinds of steel E
It is given in Table 1 with V constituent.
Steel V constituent corresponds to " known to iron-titles of titanium Nikro 128 ", for example in above-mentioned disclosure herein
Described in steel constituent.The operating procedure completed during two kinds of steel E, V powder metallurgically manufacturing, which corresponds to, generally to exist
" the operating procedure implemented in the metallurgical manufacture of iron-steel of titanium Nikro 128 ".These operating procedures are in above-mentioned specialty text
Offer middle explanation.
After powder metallurgically manufacturing, steel E and V sample P E1, PV1 are heat-treated, and the heat treatment is also corresponded to
The heat treatment that iron-Playsization of titanium Nikro 128 are implemented.Therefore, sample P E1 and PV1 are first in a vacuum in 850 DEG C of temperature
The lower duration kept by two to four hours will simultaneously then quench under with the nitrogen atmosphere of the pressure-loaded of 1-4.5 bars.With
After carry out time cured processing, wherein, sample P E1, PV1 is shelved into six to eight hours at a temperature of 480 DEG C respectively.
Fig. 1 shows the scanning electron microscopy in the steel E according to the present invention of such standard heat treatment sample P E1 section
A part for photo.Metallic matrix can be seen that by bright region, and shown and be mingled with around the TiC of matrix with dead color
Thing.
Other sample Ps E2, PV2 being made up of steel E and V carry out continuing same 2-4 hours soft annealing at 850 DEG C.
Hardening phase content is determined on sample P El, PVl, PE2, PV2.In the sample being made up of the steel according to the present invention
In PE1, PE2, hardening phase content is average more than 30 weight %, on the contrary, the sample P V1, PV2 that are made up of compared steel V are average
With only 30 weight % hardening phase.
Implement five firmly according to DIN EN ISO6508-1 to determine different sample P El, PE2, PVl, PV2 hardness
Degree measurement.So it is given in Table 2 for the average value of sample P El, PE2, PVl, PV2 measured value determined.It was shown that according to
The hardness of sample P El, PE2 of the present invention is respectively higher than the hardness of comparative sample.
In addition, the thermal conductivity λ (T) relevant with temperature by round-about way at room temperature, 100 DEG C, 200 DEG C, at 300 DEG C
It is determined that：
λ (T)=a (T) × ρ (T) × c ρ (T)
Wherein a (T)：The thermal conductivity measured by laser flash (Laserflash), such as in Linseis
GmbH：Specification LFA 1250/1600- laser flashes：The constant analyzer of heat, 2010 or ASTM International E
1461-01：By the standard method of test of the thermal diffusivity of flicker method, explained in 2001；
ρ(T):The density of each sample, passes through dilatometer measurement；
cρ(T):The specific isobaric heat capacity of sample, passes through dynamic DSC (Dynamische
Differenzkalorimetrie, " DSC ") determine.
Figure 2 illustrates the result of these tests for sample P E1 and PV1.It has been shown that by the steel according to the present invention
Thermal conductivity in the sample P E1 that E is made is respectively lower than the sample P V1 being made up of compared steel V.According to sample P E1's of the invention
It is favourable in terms of smaller thermal conductivity default steel E and V here application purpose.
It is respectively to be more than 30 weight % according to the sample P E1, PE2 of the present invention TiC contents as provided in table 1.
Density by the sample P E1, PE2 being made of the steel E according to the present invention is 6.55g/cm3, thus reached theoretical close
Degree.Do not have residual porosity rate as can be seen that the institutional framework in Fig. 1.
The electric current implemented on the sample P V1 being made by the sample P E1 being made of the steel E according to the present invention and by compared steel V is close
The result of degree-potential measurement figure 3 illustrates.Wherein, it is used as solid line for the sample P E1 current density-potential curves determined
Show and be directed to the current density-potential curve of sample P V1 determinations as shown in phantom.Current density-potential curve is in anaerobic
0.5 molar concentration sulfuric acid in measure, there is 600mV/h potential change speed at 20 DEG C relative to calomel reference electrode.
In addition, for being less than 5 μ A/cm in each case according to the sample P E1 of the present invention passive current densities determined2。
For the sample P E1 being made up of the steel E according to the present invention, surveyed by the Vltrasonic device relevant with acoustic wave propagation velocity
Modulus of elasticity is determined for 318GPa.Relatively, conventional sample PV1 modulus of elasticity is 294GPa.
Table 3 gives the overview of steel E thermal expansion.Thermal expansion passes throughDilatometer 100 DEG C until 600 DEG C most
Measured in the temperature span of high-temperature.As can be seen that thermalexpansioncoefficientαthIn 7 and 12 × 10-6Temperature range between/K
It is interior.In addition, Fig. 4 schematically illustrates the knot that dilatometer is measured on the sample P E1 by being made according to the steel of the present invention
Really, which confirms the result.
| Steel | Cr | Mo | Ni | Co | Cu | Ti | Al | TiC | NbC |
| E | 13.5 | 7.0 | 5.0 | 9.0 | 0.8 | 1.0 | 1.2 | 33 | 2.5 |
| V | 13.5 | 5.0 | 4.0 | 9.0 | 0.8 | 1.0 | 1.0 | 30 | - |
In terms of weight %, remaining iron and inevitable impurity
Table 1
| Sample | Average hardness HRC |
| PE1 | 65 |
| PV1 | 62 |
| PE2 | 54 |
| PV2 | 53 |
Table 2
| Temperature [DEG C] | αth |
| 100 | 8.4 |
| 200 | 8.7 |
| 300 | 9.0 |
| 400 | 9.2 |
| 500 | 9.4 |
| 600 | 9.7 |
Table 3.
Claims (18)
1. a kind of steel for being used to require the application of high-wearing feature, high rigidity, good corrosion resistance and/or low heat conductivity,
- wherein, the steel has at least 56HRC hardness in the state of hardening,
- wherein, there is at least 30 weight % hardening phase altogether in the institutional framework of the steel, the hardening is except TiC
It is made up of outside particle other carbonized particles, oxidation particle or nitridation particle,
- wherein, the content of TiC particles is at least 20 weight %,
And
- wherein, hardening is mutually embedded into matrix, and described matrix is by (in terms of weight %)
9.0-15.0% Cr,
5.0-9.0% Mo
3.0-7.0% Ni,
6.0-11.0% Co,
0.3-1.5% Cu,
0.1-2.0% Ti,
0.1-2.0% Al,
Remaining iron and inevitable impurity composition.
2. steel according to claim 1, it is characterised in that its Cr content is 12.5-14.5 weight %.
3. the steel according to any one in the claims, it is characterised in that its Mo content is 6.5-7.5 weight %.
4. the steel according to any one in the claims, it is characterised in that its Ni content is 4.5-5.5 weight %.
5. the steel according to any one in the claims, it is characterised in that its Co content is 8-10 weight %.
6. the steel according to any one in the claims, it is characterised in that its Cu content is 0.5-1.0 weight %.
7. the steel according to any one in the claims, it is characterised in that its Ti content is 0.8-1.2 weight %.
8. the steel according to any one in the claims, it is characterised in that its Al content is 1.0-1.4 weight %.
9. the steel according to any one in the claims, it is characterised in that its TiC content is minimum 20 volume %.
10. the steel according to any one in the claims, it is characterised in that it contains maximum to 4.5 weight %'s
NbC particles.
11. steel according to claim 10, it is characterised in that the content of NbC particles is minimum 2.0 weight %.
12. the steel according to any one in the claims, it is characterised in that the proportion of phase is hardened in its institutional framework
For minimum 30 weight %.
13. the steel according to any one in the claims, it is characterised in that its TiC content is the weight % of highest 45.
14. the steel according to any one in the claims, it is characterised in that the steel has big after the heat treatment
In 62HRC hardness, in the heat treatment, the steel are heated 2-4 hours under vacuo, then with 1-4.5 bars
Quench and then shelved at 480 DEG C 6-8 hours under the nitrogen atmosphere of pressure.
15. the steel according to any one in the claims, it is characterised in that the steel is implemented to pass through at 850 DEG C
There is at least 50HRC hardness after the soft annealing of 2-4 hours.
16. the steel according to any one in the claims, it is characterised in that the steel is made with powder metallurgic method.
17. the application of the steel according to any one in the claims, it is applied to the manufacture of component, and the component is used
In the circulation of plastic product or reproduction.
18. application according to claim 17, the component is orifice plate or the cutting knife for cutting plastic components.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| DE102014112374.3 | 2014-08-28 | ||
| DE102014112374.3A DE102014112374A1 (en) | 2014-08-28 | 2014-08-28 | Steel with high wear resistance, hardness and corrosion resistance as well as low thermal conductivity and use of such a steel |
| PCT/EP2015/069477 WO2016030396A1 (en) | 2014-08-28 | 2015-08-26 | Steel with high wear resistance, hardness and corrosion resistance and low thermal conductivity, and use of such a steel |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN107075624A true CN107075624A (en) | 2017-08-18 |
Family
ID=54014808
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201580046492.0A Pending CN107075624A (en) | 2014-08-28 | 2015-08-26 | The application of steel and this kind of steel with high wearability, hardness, corrosion resistance and low heat conductivity |
Country Status (9)
| Country | Link |
|---|---|
| US (1) | US20180119257A1 (en) |
| EP (1) | EP3186405B1 (en) |
| JP (1) | JP6210502B1 (en) |
| KR (1) | KR20170041276A (en) |
| CN (1) | CN107075624A (en) |
| BR (1) | BR112017002127A2 (en) |
| DE (1) | DE102014112374A1 (en) |
| RU (1) | RU2674174C2 (en) |
| WO (1) | WO2016030396A1 (en) |
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| EP3263726A1 (en) * | 2016-06-29 | 2018-01-03 | Deutsche Edelstahlwerke GmbH | Fe basis material and method for its production |
| JP7287916B2 (en) * | 2020-03-12 | 2023-06-06 | 株式会社神戸製鋼所 | LAMINATED PRODUCT MANUFACTURING METHOD AND LAMINATED PRODUCT |
| CN111455274A (en) * | 2020-04-08 | 2020-07-28 | 鞍钢股份有限公司 | 80 Ksi-grade 9Cr fireflood heat production well pipe and manufacturing method thereof |
| CN112251749B (en) * | 2020-10-23 | 2023-04-07 | 黑龙江科技大学 | Method for preparing ceramic phase enhanced high-entropy alloy wear-resistant coating of directional array by plasma cladding |
| KR20220063626A (en) * | 2020-11-10 | 2022-05-17 | 한국재료연구원 | TiC particle-reinforced Fe-based composite material and its manufacturing method |
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| DE3015709A1 (en) * | 1980-04-24 | 1981-10-29 | Thyssen Edelstahlwerke AG, 4000 Düsseldorf | HARD MATERIAL ALLOY |
| JPS6173867A (en) * | 1984-09-14 | 1986-04-16 | Mitsubishi Metal Corp | Hot wear resistant member of dispersion strengthening sintered alloy steel |
| JP2000273503A (en) * | 1999-03-25 | 2000-10-03 | Kobe Steel Ltd | Hard particle-dispersed sintered steel and its production |
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| JPH0586435A (en) * | 1991-09-27 | 1993-04-06 | Hitachi Metals Ltd | Tool parts material having high corrosion resistance and high wear resistance |
| SE9604538D0 (en) * | 1996-12-10 | 1996-12-10 | Hoeganaes Ab | Agglomerated iron-based powders |
| US6521353B1 (en) * | 1999-08-23 | 2003-02-18 | Kennametal Pc Inc. | Low thermal conductivity hard metal |
| SE529041C2 (en) * | 2005-08-18 | 2007-04-17 | Erasteel Kloster Ab | Use of a powder metallurgically made steel |
| SE528991C2 (en) * | 2005-08-24 | 2007-04-03 | Uddeholm Tooling Ab | Steel alloy and tools or components made of the steel alloy |
| SE533988C2 (en) * | 2008-10-16 | 2011-03-22 | Uddeholms Ab | Steel material and process for making them |
| RU2443795C2 (en) * | 2010-04-16 | 2012-02-27 | Тамара Федоровна Волынова | MULTI-FUNCTION ANTIFRICTION NANOSTRUCTURE WEAR-RESISTANT DAMPING ALLOYS WITH SHAPE MEMORY EFFECT ON METASTABLE BASIS OF IRON WITH STRUCTURE OF HEXAGONAL ε-MARTENSITE, AND ITEMS USING THESE ALLOYS WITH EFFECT OF SELF-ORGANISATION OF NANOSTRUCTURE COMPOSITIONS, SELF-STRENGTHENING AND SELF-LUBRICATION OF FRICTION SURFACES, WITH EFFECT OF SELF-DAMPING OF VIBRATIONS AND NOISES |
| EP2662460A1 (en) * | 2012-05-07 | 2013-11-13 | Valls Besitz GmbH | Tough bainitic heat treatments on steels for tooling |
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2014
- 2014-08-28 DE DE102014112374.3A patent/DE102014112374A1/en not_active Withdrawn
-
2015
- 2015-08-26 US US15/507,004 patent/US20180119257A1/en not_active Abandoned
- 2015-08-26 KR KR1020177008168A patent/KR20170041276A/en not_active Application Discontinuation
- 2015-08-26 BR BR112017002127A patent/BR112017002127A2/en not_active Application Discontinuation
- 2015-08-26 CN CN201580046492.0A patent/CN107075624A/en active Pending
- 2015-08-26 JP JP2017502268A patent/JP6210502B1/en active Active
- 2015-08-26 EP EP15756892.4A patent/EP3186405B1/en active Active
- 2015-08-26 RU RU2017106319A patent/RU2674174C2/en not_active IP Right Cessation
- 2015-08-26 WO PCT/EP2015/069477 patent/WO2016030396A1/en active Application Filing
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|---|---|---|---|---|
| US3966423A (en) * | 1973-11-06 | 1976-06-29 | Mal M Kumar | Grain refinement of titanium carbide tool steel |
| DE3015709A1 (en) * | 1980-04-24 | 1981-10-29 | Thyssen Edelstahlwerke AG, 4000 Düsseldorf | HARD MATERIAL ALLOY |
| JPS6173867A (en) * | 1984-09-14 | 1986-04-16 | Mitsubishi Metal Corp | Hot wear resistant member of dispersion strengthening sintered alloy steel |
| JP2000273503A (en) * | 1999-03-25 | 2000-10-03 | Kobe Steel Ltd | Hard particle-dispersed sintered steel and its production |
| CN101517112A (en) * | 2006-08-11 | 2009-08-26 | 联邦-蒙古尔烧结产品有限公司 | Improved powder metallurgy composition |
| CN102822367A (en) * | 2010-02-05 | 2012-12-12 | 伟尔矿物澳大利亚私人有限公司 | Hard metal materials |
Also Published As
| Publication number | Publication date |
|---|---|
| RU2017106319A (en) | 2018-08-28 |
| WO2016030396A1 (en) | 2016-03-03 |
| KR20170041276A (en) | 2017-04-14 |
| RU2674174C2 (en) | 2018-12-05 |
| BR112017002127A2 (en) | 2017-11-21 |
| JP2017532434A (en) | 2017-11-02 |
| EP3186405B1 (en) | 2018-10-03 |
| US20180119257A1 (en) | 2018-05-03 |
| EP3186405A1 (en) | 2017-07-05 |
| JP6210502B1 (en) | 2017-10-11 |
| DE102014112374A1 (en) | 2016-03-03 |
| RU2017106319A3 (en) | 2018-08-28 |
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