CN101426944A - High-speed steel for saw blades - Google Patents

High-speed steel for saw blades Download PDF

Info

Publication number
CN101426944A
CN101426944A CNA2007800143060A CN200780014306A CN101426944A CN 101426944 A CN101426944 A CN 101426944A CN A2007800143060 A CNA2007800143060 A CN A2007800143060A CN 200780014306 A CN200780014306 A CN 200780014306A CN 101426944 A CN101426944 A CN 101426944A
Authority
CN
China
Prior art keywords
niobium
vanadium
steel
rapid steel
saw blade
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Pending
Application number
CNA2007800143060A
Other languages
Chinese (zh)
Inventor
C·A·巴伯萨
R·A·麦斯奎他
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Villares Metals S A
Villares Metals SA
Original Assignee
Villares Metals S A
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Villares Metals S A filed Critical Villares Metals S A
Publication of CN101426944A publication Critical patent/CN101426944A/en
Pending legal-status Critical Current

Links

Images

Classifications

    • 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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/24—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for saw blades
    • 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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • 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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • 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
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • 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
    • C22C38/30—Ferrous alloys, e.g. steel alloys containing chromium with cobalt
    • 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
    • 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
    • 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
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • 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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
  • Forging (AREA)
  • Cutting Tools, Boring Holders, And Turrets (AREA)

Abstract

High-speed steel for saw blades, presenting a composition of alloy elements consisting, in mass percentage, of Carbon between 0.5 and 1.5; Chromium between 1.0 and 10.0; equivalent Tungsten, given by 2Mo+W relation, between 3.0 and 10.0; Niobium between 0.5 and 2.0. Niobium may be partially or fully replaced with Vanadium, at a ratio of 2% Niobium to each 1% Vanadium; Vanadium between 0.3 and 2.0. Vanadium may be partially or fully replaced with Niobium, at a ratio of 2% Niobium to each 1% Vanadium, Silicon between 0.3 and 3.5. Silicon may be partially or fully replaced with Aluminum, at a 1:1 ratio; Cobalt lower than 8, the remaining substantially Fe and impurities inevitable to the preparation process.

Description

The rapid steel that is used for saw blade
The invention relates to a kind of steel that is used for the processing of cutting tool and metal and other material.Described steel has the composition that it is classified as the high-speed type tool steel, its valuable alloying element that mainly is to use lower aq is vanadium, tungsten and molybdenum for example, but performance is equivalent to or is higher than those performances of the conventional rapid steel of less alloying, and is worse than those performances of the conventional rapid steel of bigger alloying a little.By for for example use of silicon and aluminium of the alloying elements nb of usefulness and lower-cost alloying element, obtained this performance configuration.
Cutting tool is applied in a lot of cuttings and the process operation.Some examples are in machining steel, non-ferrous alloy or other solid material in other form, the cutting operation that carries out with band (tape) saw, automatic or manual saw, creep into, turning, tapping, milling.The important example of the application that the present invention means is a saw, this saw is used for machine or manual free-cutting saw, and both all can use according to hard form, are entirely rapid steel, or bimetallic, having just, the tooth zone of rapid steel reaches other zone of being made by the low-alloy engineering steel.Other cutting tool typically uses rapid steel and them to be made by steel of the present invention, and what belong to them has: wimble, vertical milling machine (top milling), copying tool (profile tool), tack pricker (tack), cutter head (bit) and be used for the special awl of highly resistant material.In addition, also has the thinly-sliced instrument of cutting, for example screwtap, screw plate (die) and special milling cutter (mill).
The same high-speed steels that these instruments use can be used as shaping (conforming) instrument.Example is stamping machine, the instrument that is used for cold forging, cutting die and shear, stamping die, be used for mould, the plug-in unit that is used for forge hot and warm forging and the instrument thereof of metal (postmetallic) after the shaping or pottery, and other of cold shaping, warm shaping or hot shaping instrument in using, wherein the material of shaping has and reaches 1300 ℃ temperature at the most.
The steel that tradition is used for cutting tool is a rapid steel, and its principal character is that high wear resistance and hardness at high temperature keep.Typical example is AISI M or AISI T Series Steel, and outstanding steel is AISI M2, M7 and TI.The steel of less alloying can be used for the less instrument of requirement; Main steel is DIN 1.3333 and AISI M50 and M52 steel.Be displayed in Table 1 the chemical constitution of these steel, wherein emphasis must be placed on final cost of alloy is had on tungsten, molybdenum and the vanadium of large portion contribution.As the normalization method of being undertaken by the cost of alloy in December, 2005, in table 2, listed of the influence of these elements to cost.Aspect cost of alloy, according to this tittle, the advantage that the steel of less alloying surpasses conventional steel is clearly.
Therefore, rapid steel has strong influence aspect the cost of they and raw material (alloying element) costs associated usually.Yet, the increase of steel and iron alloy cost recently make itself in addition more remarkable.In many application, even the steel of less alloying also has the intensive cost impact, thereby increased having even the interest of the composition of low alloyed element content more.And, about conventional steel, having increased the demand of the steel of less alloying, the steel of this less alloying does not have this expression power performance loss, and hardness is their salient features.Minimum hardness during great majority are used is 64HRC, and as shown in table 1, steel M50 and M52 do not satisfy this requirement.
Table 1: the 3%V steel (ET) that comprises in the prior art.Only providing main alloy element, is iron in mass percent and surplus.
Figure A200780014306D00061
* calculate (W+Mo+V) summation by formula 0.7Mo+0.4V+0.3W.These are and the relevant index of each element cost of in December, 2005.
Therefore, obviously need new rapid steel to form, this composition can satisfy the requirement of low levels alloying element, described content even be lower than existing steel, reach the minimum hardness of 64HRC and have the suitable distribution of insoluble carbide, obtain to use desired performance thus.
Steel of the present invention satisfies these requirements.
Purpose of the present invention primarily is the influence that research has silicon, aluminium and niobium element in the composition of vanadium, molybdenum and tungsten of low levels.The vital role of niobium obtains affirmation in this research, yet is not enough to produce the hardness of desired level.In steel of the present invention, use aluminium then and use element silicon especially, demonstrated unusual effect.Therefore, the qualification of these constituent contents and their enough work range have promoted obtaining of predicted performance in the reduction of cost and the material.Hereinafter these scopes are described and the effect of each element is summarized.
In order to satisfy condition mentioned above, the alloying element composition that steel of the present invention has is made of following in mass percent:
0.5-1.5C preferred 0.8-1.1C typically is 0.87C.
1.0-7.0C preferred 3.0-5.0C typically is 4.0C.
3.0-10.0 W Equivalence(equivalent tungsten), W EquivalenceBy relational expression W Equivalence=W+2.0Mo provides, and is preferably the W of 4.0-8.0 Equivalence, typically be 6.0 W Equivalence
0.5-3.0Nb preferred 0.8-1.8Nb typically is 1.2Nb, and Nb can carry out partly or entirely substituting with Zr, Ti, Ta or V, wherein the pass of being complied with is the corresponding 0.5%V of 1.0%Nb or Ti and corresponding 1.0%Zr of 1.0%Nb or Ta.
0.3-2.0V preferred 0.5-1.0V typically is 0.7V, and V can carry out partly or entirely substituting with Nb, wherein the ratio of being complied with is the corresponding 0.5%V of 1.0%Nb.Substituting with Nb in the situation of V, the content of final Nb must calculate and add in the content that alloy stipulated by this relational expression in the alloy.
0.3-3.5Si preferred 0.7-2.0V typically is 1.0Si, and Si can be with Nb with the 1:1 proportional part or substitute fully.
Maximum 8% Co, preferred maximum 5% cobalt, typically maximum 2% Co.
As described below, can in steel of the present invention, add aluminium, thereby promote advantageous property.Yet the composition that does not add aluminium also can be used for steel of the present invention, because it is more or less freely at the alloy manufacture view.Therefore aluminium content should be performed as follows dispensing:
For with the composition of Al as residual element, maximum 1.0 Al, preferred maximum 0.5 Al, typically maximum 0.2 Al.In this case, Al should treat as impurity.
For needing Al to improve the composition of performance, 0.2-3.5Al, preferred 0.5-2.0Al typically is 1.0Al, adds above-mentioned Si content.
Surplus is inevitably metal or a nonmetallic impurity in iron and the steel rolling process, and wherein said impurity includes but not limited to down surface element, in mass percent:
Maximum 1.5 Mn, preferred maximum 0.8 Mn, typically maximum 0.5 Mn.
Maximum 0.10 P, preferred maximum 0.05 P, typically maximum 0.03 P.
Maximum 0.10 S, preferred maximum 0.020 S, typically maximum 0.008 S.
Maximum 0.1 N, preferred maximum 0.05 N, typically maximum 0.5 N.
Maximum 0.5 Ce, or other rare earth element.Group of the lanthanides in the periodic table of elements or actinide elements, and think that La, Ac, Hf and Rf element are rare earth elements.Ce content should preferably be lower than 0.1, and typically is lower than 0.06.
The cause description that the material that face is new is as follows formed.Shown percentage ratio relates to mass percent.
C: carbon is heat treatment response and the main ingredient that forms primary carbide.Its content should be lower than 1.5%, preferably is 1.1% to the maximum, and the retained austenite that makes the quenching back exist is not very high.In this steel in less alloying (as a kind of steel of the present invention) is important, because carbon is tending towards forming a less thing (primary) or the alloying element carbide of eutectic form; Therefore, after quenching, obtain the free carbon of high level, thereby help the retained austenite fractional to significantly improve.Yet carbon content should be enough to combine the formation primary carbide especially with niobium during tempering, and forms proeutectoid carbide, and promotes martensitic sclerosis after quenching.Therefore, carbon content should be not less than 0.5%, and it is preferred being higher than 0.8% carbon.
Cr: chromium content should be higher than 1%, preferably is higher than 3%, because this element helps separating out of quenching characteristics and proeutectoid carbide during tempering and annealing.Chromium has also determined M with carbon 7C 3The formation of type primary carbide, this is unwanted for rapid steel, because they reduce rectification capacity (rectification capacity) and toughness.Therefore, chromium content should be limited to 10%, preferably is lower than 7%.
W and Mo: tungsten and molybdenum have similar action to rapid steel, particularly exist with the M2C type of same type or M6C type primary carbide and proeutectoid carbide, and the latter is during the tempering or slightly solidifying under (gross solidification) condition and form.Therefore, their equivalent tungsten relational expression (W that can provide by the W+2Mo summation Equivalence) and stipulated that jointly described equivalent relation formula has been carried out normalization method to two kinds of atoms of elements amount differences.For the present invention, special estimate to use molybdenum and tungsten, in order to during tempering, forming proeutectoid carbide, thereby promote tempered-hardness.Therefore, separate out and hardness W for the secondary of enough volumes after the tempering EquivalenceMust be higher than 3%, preferably be higher than 4%.On the other hand, these elements produce remarkable influence to the cost of alloy, so the minimizing of these elements is one of main aspects of steel of the present invention.So W Equivalence contentShould be lower than 10.0%, preferably be lower than 8.0%.
V: for steel of the present invention, when secondary hardening vanadium should have with regard to the molybdenum function suitable with the described function of tungsten effect, thereby when tempering, form the carbide of tiny (thin).Vanadium also can form primary carbide, but this is not to add it in the steel main purpose in the present invention.During austenitizing, vanadium also has other remarkable influence to the growth control of austenite crystal.For these effects, vanadium should be higher than 0.3%, preferably is higher than 0.5%.Because this also is the important origin cause of formation in cost of alloy, content of vanadium of the present invention should be lower than 2.0%, preferably is lower than 1.0%.
Nb: niobium has material impact to steel of the present invention.Therefore this element mainly forms the hard low eutectic carbides of MC type height, and they are important for the abrasion resistance of prepared instrument.The attractive effect of another of niobium is that the MC carbide of formation makes little tungsten, molybdenum and vanadium dissolving, makes that these elements freely secondary are separated out after austenitizing and quenching.Therefore, the rapid steel related with niobium allows to use molybdenum, tungsten and the vanadium of low amount, and therefore this element plays remarkable effect to reducing cost of alloy.Yet its performance is guaranteed by the mark of the tiny and highly hard MC carbide that formed by niobium.On the other hand, content of niobium can not be higher than 3%, because it forms primary carbide and thick carbide under these situations, these carbide almost can not be handled by hot shaping and carry out refinement.Therefore, the too much content of niobium also can damage the toughness and the rectification capacity of alloy except that the cost that increases alloy.Thereby the content of niobium in the steel of the present invention should be 0.5-3.0%, preferred 0.8-1.8%.
Si: silicon is the one of the chief elements of steel of the present invention.This element once all has undesirable influence with proeutectoid carbide to the rapid steel of big alloying usually.In these influences, the increase of primary carbide volume is main influence, this influence infringement rectification capacity and heat treatment response, and reduce tempering resistance.Occur be like this because solidificating period silicon to the influence of delta ferrite volume, and the reducing of high stability MC type and MC2 type proeutectoid carbide volume.Therefore, it does not add in usually forming and is higher than 0.5%.Yet steel of the present invention does not have the negative issue about the introducing of silicon, and this is because it is the steel of less alloying.On the contrary, this element causes significantly improving of tempered-hardness.This effect fully do not explained, but it should be that silicon causes the effect of the elimination of the cementite of separating out during by tempering, thereby promotes the increase of MC type and MC2 type carbide amount.Therefore, although promote the element of secondary hardening such as the minimizing of tungsten, molybdenum and vanadium, the increase of silicone content has promoted the recovery and the lifting of hardness in the steel of the present invention, till obtaining acceptable value for rapid steel.For these effects, silicone content must be higher than 0.3%, preferably is higher than 0.7%.Yet the content of this element must be lower than 3.5%, and this is because it reduces the austenitizing scope and cause ferrite to show sclerosis when annealing.The content of silicon must preferably be lower than 2.0%.
Al: the interpolation of aluminium is chosen wantonly for steel of the present invention.Along with content is higher than 0.3%, preferably is higher than 0.7%, the performance that can obtain slightly increases (gain), for example tempering resistance.Yet, in order to promote hyperergy and the AC in ferritic high sclerosis, the liquid steel 1And AC 3The raising of temperature, aluminium must be lower than 3.5%, preferably is lower than 2.0%.Even at content near 1.0% o'clock, aluminium still causes these undesired effects.AC 1And AC 3Variation of temperature makes the condition of anneal of material become difficult especially, needs significantly higher temperature.And with regard to the non-metallic inclusions of the final steel that obtained, the reactivity of liquid metal makes the running of rolling mill and the cleaning difficulty that becomes.Therefore, the steel of the present invention aluminum that can also remain content gets.In this case, aluminium must be lower than 1.0%, preferably is lower than 0.5%.
Residuum: other element for example manganese, nickel and copper and usually as obtain from the typical residuum of liquid steel preparation process those, must be regarded as impurity, they relate to the deoxidation process in the rolling mill or are inherent for manufacturing processed.Therefore, the content of manganese, nickel and copper is limited to 1.5%, preferably is lower than 1.0%.Element segregation on grain contours and other interface such as p and s.Therefore, phosphorus must be lower than 0.10%, preferably be lower than 0.5%, and sulphur must be lower than 0.050%, preferably be 0.020% to the maximum.
As mentioned above, in product such as coiled material, bar, wire rod, sheet material and band, by no matter being ordinary method or special methods, for example powder metallurgy, injection shaping (sprayconforming) or continuous casting can be made alloy with rolled products or forging product form.
In the description of the experiment of being carried out accompanying drawing has been done reference below, wherein:
Fig. 1 has shown the fusion gross microstructure (fusion grossmicrostructure) of prior art alloy ET1, has shown the X ray distribution image of vanadium, tungsten and molybdenum element.In this distribution image, dot density is high more, and the relative concentration of chemical element is high more.By scanning electron microscopy (SEM) is that secondary electron obtains microstructure; Obtain the X ray distribution image by WDS.
Fig. 2 has shown the fusion gross microstructure of prior art alloy ET2, has shown the X ray distribution image of vanadium, tungsten and molybdenum element.In this distribution image, dot density is high more, and the relative concentration of chemical element is high more.By scanning electron microscopy (SEM) is that secondary electron obtains microstructure; Obtain the X ray distribution image by WDS.
Fig. 3 has shown the fusion gross microstructure of alloy PI1 of the present invention, has shown the X ray distribution image of vanadium, tungsten, molybdenum and niobium element.In this distribution image, dot density is high more, and the relative concentration of chemical element is high more.By scanning electron microscopy (SEM) is that secondary electron obtains microstructure; Obtain the X ray distribution image by WDS.
Fig. 4 has shown the fusion gross microstructure of alloy PI2 of the present invention, has shown the X ray distribution image of vanadium, tungsten, molybdenum and niobium element.In this distribution image, dot density is high more, and the relative concentration of chemical element is high more.By scanning electron microscopy (SEM) is that secondary electron obtains microstructure; Obtain the X ray distribution image by WDS.
Fig. 5 has shown the fusion gross microstructure of alloy PI3 of the present invention, has shown the X ray distribution image of vanadium, tungsten, molybdenum and niobium element.In this distribution image, dot density is high more, and the relative concentration of chemical element is high more.By scanning electron microscopy (SEM) is that secondary electron obtains microstructure; Obtain the X ray distribution image by WDS.
Fig. 6 has shown the alloy temper curve.For ET2, PI1, PI2 and PI3 alloy, study, discerned the curve of two kinds of austenitizing temperatures in the upper right corner of each curve.The ET1 alloy is equivalent to austenitizing at 1200 ℃, because this temperature common austenitizing temperature that is it.With the negative pressure of about 15mm, make specimen shown in stand austenitizing under the temperature, kept 5 minutes in this temperature, oil quenching and double tempering 2 hours, obtain the result of specimen.
Fig. 7 is with a) absolute value and b) the percentage ratio carbide size that contrasted ET2, PI1, PI2 and PI2 alloy distributes.The result analyzes (the area total 0.15mm that is analyzed in each alloy with 12 visual fields with 1000 times of enlargement ratios 2) obtain.
Fig. 8 after 4% nitric acid Nai Taer ethanol corrosive fluid (nital) corrodes, has contrasted the microstructure of representing following each alloy: ET2, PI1, PI2 and PI3 under the quenching and tempered condition at peak value of hardness place.500 times of enlargement ratios.
Embodiment 1:
In order to compare, prepared the experiment billet of two kinds of steel of prior art, called after ET1 and ET2 with experiment billet of the present invention (called after PI1, PI2 and PI3).Steel ET1 is similar to high C AISI M2 corresponding to DIN 1,3343, is widely used in the instrument that rapid steel is made, and owing to this reason, as the reference of material of the present invention.On the other hand, steel ET2 is the steel of less alloying, can reach 64 HRC and perform well in saw, is on the cutting edge.Be displayed in Table 2 chemical constitution.Owing to carried out normalization method by cost, also to the higher cost element for example the summation of tungsten, molybdenum and vanadium quantize.
Table 2 has shown the remarkable minimizing of the element of Steel Alloy of the present invention, and this is converted to the contrast (number in December, 2005 calculates) of the alloy of lower cost-as being carried out in the table 3.Can be observed the described minimizing that is taken place to the ET2 steel from the ET1 steel of prior art, and can be observed the described minimizing under same ratio ET2 steel, this is that this steel is the steel of less alloying because for steel of the present invention.Therefore, these results show, about the steel of existing less alloying ET2 for example, steel of the present invention is at second (second) step that reduces cost of alloy.And about the ET1 steel, the difference of cost of alloy has twice big.
For these five kinds of alloys, in vacuum induction furnace, carry out billet fusing, and be poured into iron and water in the injection molding with the method for sealing, produce the 55kg billet.After solidifying, described billet is carried out subcritical annealing, and these five kinds of compositions are carried out preliminary classification about fusion gross microstructure.At first, in the ET1 alloy, can see the primary carbide of higher amount, promptly cause by the alloying element of its high level.Secondly, according to the dot density in the radioscopic image, the concentration of vanadium, molybdenum and W elements is clearly, and about PI1, PI2 and PI2 alloy, higher in the carbonization of this concentration in ET1 and ET2 alloy.On the one hand, the former is tending towards forming main niobium composition.Therefore these carbide are MC types, and are highly hard, the higher element of the alternative cost carbide of tungsten, molybdenum and vanadium for example well.And in addition, niobium carbide has attractive feature: they do not have other element, particularly molybdenum, tungsten and the vanadium of expression power amount.
Therefore, they provide the bigger degree of freedom that forms proeutectoid carbide for these elements, and these carbide are used needed high rigidity for the inspection material during tempering be important.
In brief, Fig. 1 to 5 shows that the primary carbide of PI1, PI2 and PI3 alloy mainly is the MC type and is rich in niobium.These carbide are than tungsten, molybdenum and the vanadium of the lower amount of primary carbide consumption of prior art steel, and therefore they allow to reduce the total content of these elements in alloy, and this wants by steel of the present invention just.
Table 2: the chemical constitution of four kinds of steel (ET1 to ET4) of prior art and steel of the present invention (PI)
* through type 0.7Mo+0.4V+0.3W calculates the summation of (W+Mo+V).These are and the relevant index of each element cost of in December, 2005.Owing to carried out normalization method by the ET2 steel, provided described summation with relative (relat.) value with absolute (abs.) value.
Except that primary carbide, the hardness after the thermal treatment also is important for rapid steel.Therefore, to be rolled into diameter be the round bar of 34-mm and anneal with the experiment billet, is 850 ℃ of levels for ET1, ET2 and ET3 alloy, and be 980 ℃ of levels for the PI3 alloy.Then, they are carried out quench treatment, carried out austenitizing 5 minutes at 1185-1200 ℃, and carry out double tempering at 450 ℃ and 600 ℃, each kept 2 hours.
Table 3: metal fill (metallic load) is the cost of the alloyed metal that comprised of ET1, ET2, PI1, PI2 and PI3 alloy.The cost of the metal fill by alloy ET1 and numerical value is carried out normalization method for ET2.These calculating relate to the production that undertaken by the electric steel milling train in December, 2005.
T1 T2 T3 12 13
The cost of the metal that is comprised in the alloy carries out normalization method in two ways. 00 9.2 3.4 3.4 3.6
69 00 6.4 6.4 6.8
Table 4 has shown ET1, ET2, PI1, PI2 and the PI3 steel hardness after quenching and tempering that provides among Fig. 6 with diagrammatic form.Steel-the ET2 of less alloying, PI1, PI2 and PI3 carry out austenitizing at 1185 ℃ and 1200 ℃.Steel for big alloying is ET1, and the general austenitizing temperature that only is used for this material is 1200 ℃.
Result's hint among table 4 and Fig. 6, PI1 of the present invention and PI2 steel can (manage to) reach the hardness that is higher than 64HRC, are attractive alloys therefore.Material is carried out tempering under near the temperature of peak value of hardness, to be used for 550 ℃ of instruments of work down, the hardness of PI2 and PI3 steel is similar.Therefore as if, bring under the situation of higher complexity for the preparation high-aluminium alloy, PI2 forms more noticeable; And in this case, in fact hardness conform to the ET2 steel.Yet for the instrument of working under higher temperature, the PI3 alloy is tending towards promoting bigger hardness, and therefore it may be more noticeable.
In Fig. 6, for the PI3 alloy, it is obvious that PI1 and PI2 hardness of alloy improve, and this hardness raising relates to higher silicone content.This is to produce owing to influence that silicon is separated out secondary, may be because the increase of the volume of the MC type of the minimizing of M3C type proeutectoid carbide and refinement more and M2C type carbide.On the other hand, between PI2 and PI3 alloy, the PI3 alloy demonstrates bigger hardness under higher tempering temperature (being higher than 550 ℃).In this case, main effect is the effect of the aluminium content of PI3 alloy, because this element works by improving the carbon activity and reducing elemental diffusion; Therefore, acquisition bigger resistance at high temperature.
Table 4: steel of prior art (ET1 and ET2) and steel of the present invention are to heat treated response.Carry out austenitizing at 1185 and 1200 ℃, in oil, quench and shown in carry out twice tempering in two hours under the temperature, obtain the HRC hardness result then.
Figure A200780014306D00151
Figure A200780014306D00161
Also the austenite grain size of ET2, PI1, PI2 and PI3 alloy is estimated with regard to some austenitizing temperatures.The result is displayed in Table 5.PI1, PI2 and PI3 steel have bigger a little grain-size than ET2 steel, because it has high content of vanadium, this content is enough to control the growth of austenite grain size fully.Yet PI1, PI2 and PI3 alloy have the grain-size that still obtains refinement, particularly before 1185 ℃, and think that 33mm thickness (gauge) is big relatively for rapid steel.Therefore, this austenitizing temperature the most suitable steel of the present invention as if.
Table 5:, record the size of austenite crystal by the Snyder-Graff division lines method for the steel that carries out austenitizing at 1185-1200 ℃.The standard deviation that index ± expression is measured.
Steel/T Austenitizing 1160℃ 1185℃ 1200℃
ET2 12.6±0.9 12.1±1.2 12.4±2.1
PI1 12.4±1.2 10.7±1.2 10.8±1.6
PI2 12.1±1.6 11.5±1.0 9.9±1.6
PI3 10.9±1.1 10.4±2.1 11.6±2.3
Except that under the thick condition of fusion, evaluating, also after hot shaping, the primary carbide of ET2 steel and steel of the present invention (PI1, PI2 and PI3) is evaluated.The result obtains by the image calculation analysis.These results show in table 6 and Fig. 7.
One of the total volume fraction of the carbide that the ET2 steel has and PI1 and PI3 steel are suitable; The PI1 steel has higher a little volume fraction.About size, the ET2 steel has less total carbides, but it has the thick carbide (surpassing 8 μ m) of comparatively high amts.
PI1, PI2 and PI3 steel have the carbide that concentrates in thin (thinner) scope, and described scope is in absolute figure and relative value.As obtaining, find out qualitatively in the microstructure of the material that these results also can show in Fig. 8 by quantitative analysis.
For rapid steel, it is attractive having thinner carbide, because they promote the bigger degree of resistance to wearing, and they play the effect of raising flexible.Thin carbide also is important for the better working ability of promotion, thereby makes rapid steel be easy to processing when fabrication tool.Therefore, the carbide of the refinement more that obtains in PI1, PI2 and PI3 steel is important for the application in the cutting tool.They particularly cause by the niobium eutectic, and the niobium eutectic has a thinner form than the primary carbide of ET2 alloy (particularly be rich in vanadium those) after hot shaping.
The quantitative analysis results of the image of microstructure in table 6:ET2, PI1, PI2 and the PI3 steel is according to carbide volume and size.The result analyzes (the area total 0.15mm that is analyzed in each alloy by 12 visual fields with 1000 times of enlargement ratios 2) obtain.
Figure A200780014306D00181
Figure A200780014306D00191
Therefore, steel described in the invention, particularly ET2 and ET3 steel have and are suitable for the low performance that requires employed Rapid Steel Tool in the situation fully.Except that cutting tool for example bore with milling attachment, the saw that uses in manual saw or the machine is the example that is adopted in the situation that requires of low working life.
The performance of steel of the present invention allows it to be used as substitute such as the ET2 steel in all these are used, and has suitable performance and significant cost reduces (seeing Table 3).Steel of the present invention is the steel of alternative bigger alloying (in this article by the representative of ET1 steel) also, may have lower performance, but the expense reduction is extremely significant.
Only use the element of lower cost by alloy designs, obtained this combination of cost and performance, purpose is the effect that strengthens noble element (tungsten, molybdenum and vanadium).
Embodiment 2
Estimate for behavior, steel of the present invention has been carried out performance test industrial application.Make the cutting tool of " hard manual saw " type and cut test.With each three a kind of blade of ET2, PI1, PI2 and PI3 alloy, carry out these tests according to standard BS1919.
Alloy PI1 of the present invention, PI2 and PI3 are made by 55kg experiment billet, through hot rolling up to 2.8 * 12mm 2Size, and then be rolled into the final size of saw.Obtain the ET2 steel by industrial admixtion, be used for reference to purpose.Select the ET2 alloy for the contrast purpose, because this is the material that tradition is used in the manual saw blade.
Test comprises, at a branch of 2.60 * 25.00mm that is of a size of 2, hardness is the stainless steel UNSS304 of 180HV, on 00, each blade carries out 10 cuttings.For all saw blades, speed is constant (70 strokes of per minutes) and cutting power is carried out identical pre-calibration.On suitable machine, test.Performance index are: average wear rate and overall average cutting time.Wear rate is characterized by and cuts the required variation (evolution) of drawing number at every turn.The number of drawing according to each cutting calculates by the first order derivative of figure with respect to the cutting number of times.Lower wear rate represents to have the saw cuts of less stroke of number, and the user feels that this is a preferable performance.Then produce identical situation for the cutting time, promptly the cutting time short more, saw blade performance is good more.For the material under the double tempering condition, the result who has obtained when being displayed in Table 7 performance test.
Table 7: the results of property of the saw blade of making by ET2, PI1, PI2 and PI3 steel, between two kinds of tempered condition, distribute.Optimum performance is the minimizing about wear rate and cutting time.
Figure A200780014306D00201
Most important condition is 540 ℃, because this uses at most in the saw of making at present.For alloy of the present invention, in case the result that they demonstrate is equivalent to or even be higher than those of prior art steel (ET2), then the result that obtains is attractive, particularly for PI2 and PI3 alloy.Because carry out tempering at 540 ℃, the alloy with PI3 has minimum wear rate; And the PI2 alloy also is like this, and it produces the shorter cutting time than ET2 alloy.
Therefore, think that PI2 and PI3 are attractive for application, because they cause the content of alloying element significantly to reduce, and although it is so, but they have promoted suitable cutting ability.As shown in table 7, these performances can even be higher than the steel of prior art.As in embodiment 1, discussing, this proper development by chemical constitution, special combination by Nb and Si element produce, described Nb and Si element are the materials that promotes high rigidity and refinement carbide, cause the more overall minimizing of expensive alloy element Mo, W and V.
Claims (according to the modification of the 19th of treaty)
1. be used for the rapid steel of saw blade, it is characterized in that, the alloying element composition of existence is made of following in mass percent: the carbon of 0.5-1.5; 1.0-10.0 chromium; 3.0-10.0 equivalent tungsten, this equivalence tungsten is provided by the 2Mo+W relational expression; 0.5-2.0 niobium; 0.3-2.0 vanadium; 0.3-3.5 silicon; Be lower than 0.5 aluminium; Be lower than 8.0 cobalt; All the other are unavoidable impurities in Fe and the preparation process substantially; This alloy is by casting billet preparation, describedly is cast into routine casting or continuous casting; And with described billet forge hot or be rolled into final size.
2. be used for the rapid steel of saw blade, it is characterized in that, the alloying element composition of existence is made of following in mass percent: the carbon of 0.5-1.5; 1.0-10.0 chromium; 3.0-10.0 equivalent tungsten, this equivalence tungsten is provided by the 2Mo+W relational expression; 0.5-2.0 niobium; 0.3-2.0 vanadium; 1.0-3.5 silicon; Be lower than 0.5 aluminium; Be lower than 8.0 cobalt; All the other are unavoidable impurities in Fe and the preparation process substantially; This alloy is by casting billet preparation, describedly is cast into routine casting or continuous casting; And with described billet forge hot or be rolled into final size.
3. be used for the rapid steel of saw blade, it is characterized in that, the alloying element composition of existence is made of following in mass percent: the carbon of 0.5-1.5; 1.0-5.0 chromium; 3.0-10.0 equivalent tungsten, this equivalence tungsten is provided by the 2Mo+W relational expression; 0.5-2.0 niobium; 0.3-2.0 vanadium; 0.7-3.5 silicon; Be lower than 0.5 aluminium; Be lower than 8.0 cobalt; All the other are unavoidable impurities in Fe and the preparation process substantially; This alloy is by casting billet preparation, describedly is cast into routine casting or continuous casting; And with described billet forge hot or be rolled into final size.
4. be used for the rapid steel of saw blade, it is characterized in that, the alloying element composition of existence is made of following substantially in mass percent: the carbon of 0.6-1.4; 3.0-5.0 chromium; 4.0-8.0 equivalent tungsten, this equivalence tungsten is provided by the 2Mo+W relational expression; 0.8-1.6 niobium; 0.5-1.0 vanadium; 0.7-2.0 silicon; Be lower than 0.5 aluminium; Be lower than 5.0 cobalt; All the other are unavoidable impurities in Fe and the preparation process substantially; This alloy is by casting billet preparation, describedly is cast into routine casting or continuous casting; And with described billet forge hot or be rolled into final size.
5. according to each the rapid steel that is used for saw blade in the claim 1 to 4, it is characterized in that, comprise, substitute the vanadium of niobium or the niobium of alternative vanadium with the ratio of Nb:V=2:1, but keeping the minimum content of niobium is 0.5 with mass percent.
6. according to each the rapid steel that is used for saw blade in the claim 1 to 5, it is characterized in that, comprise that be higher than 1.25 but be lower than 3.0 equivalent vanadium, this equivalence vanadium is provided by the V+Nb/2 relational expression with mass percent.
7. according to each the rapid steel that is used for saw blade in the claim 1 to 6, it is characterized in that, comprise with mass percent, can be by the proportional part ground of Si:Al=1:1 silicone content with the aluminium exchange, but aluminium content is 0.5 to the maximum.
8. according to each the rapid steel that is used for saw blade in the claim 1 to 7, it is characterized in that, comprise the aluminium of 0.5-2.0% in mass percent.
9. according to each the rapid steel that is used for saw blade in the claim 1 to 8, it is characterized in that, comprise the aluminium of 0.8-1.2% in mass percent.
10. according to each the rapid steel that is used for saw blade in the claim 1 to 9, it is characterized in that, comprise maximum 1.5 manganese, maximum 1.5 nickel, maximum 1.5 copper, maximum 0.10 phosphorus, maximum 0.10 sulphur and maximum 0.10 nitrogen in mass percent.
11. according to each the rapid steel that is used for saw blade in the claim 1 to 10, it is characterized in that, comprise the manganese of maximum 1.0, maximum 1.0 nickel, maximum 1.0 copper, maximum 0.5 aluminium, maximum 0.08 phosphorus, the sulphur of maximum 0.01 and maximum 0.02 nitrogen in mass percent.
12. according to each the rapid steel that is used for saw blade in the claim 1 to 11, it is characterized in that, comprise in mass percent and be lower than 1.0 cobalt.
13. according to each the rapid steel that is used for saw blade in the claim 1 to 12, it is characterized in that, comprise the manganese of maximum 0.5, maximum 0.5 nickel, maximum 0.5 copper, maximum 0.2 aluminium, maximum 0.04 phosphorus, the sulphur of maximum 0.005 and maximum 0.01 nitrogen in mass percent.
14. according to each the rapid steel that is used for saw blade in the claim 1 to 13, it is characterized in that, comprise maximum 0.5 Ce or other rare earth element in mass percent; Lanthanon in the periodictable or actinide elements and La, Ac, Hf and Rf element are thought rare earth element.
15., it is characterized in that according to each the rapid steel that is used for saw blade in the claim 1 to 14, comprise titanium, zirconium or the tantalum element that partly or entirely substitutes niobium and v element in mass percent, wherein the pass of being complied with is the corresponding 1 part of vanadium of 1 part of Ti or 0.5 part of niobium; And 1 part of Ta or the corresponding 2 parts of vanadium of Zr or 1 part of niobium.
16., it is characterized in that this rapid steel is used for cutting tool and processing according to each the rapid steel that is used for saw blade in the claim 1 to 15.
17. according to each the rapid steel that is used for saw blade in the claim 1 to 16, it is characterized in that, this rapid steel is used for the saw blade of hand and machine or saw, and they are formed by rapid steel or the bimetal type fully, and the latter comprises the cutting tip of only being made by rapid steel.
18. according to each the rapid steel that is used for saw blade in the claim 1 to 17, it is characterized in that this rapid steel is used for rotary cutting, for example wimble, milling attachment, screwtap, screw plate and be used for processing metallic or other instrument of other material.
19., it is characterized in that this rapid steel is used to have the machining tool of low working life expection, for example poor efficiency industry instrument and household appliance according to each the rapid steel that is used for saw blade in the claim 1 to 18.
20., it is characterized in that this rapid steel is used for cold integration, temperature is integrated and the process of heat integration steel, non-ferrous alloy or other solid material according to each the rapid steel that is used for saw blade in the claim 1 to 19.
21. according to each the rapid steel that is used for saw blade in the claim 1 to 20, it is characterized in that, this rapid steel makes by routine casting, continuous casting, then make the finished product size by the heat integration method, for example coiled material, bar, band and sheet material, perhaps even can under as cast condition, use described alloy.
22., it is characterized in that according to each the rapid steel that is used for saw blade in the claim 1 to 21, in mass percent, comprise the silicon of 1.0-3.5, it is prepared by comprising the broken and back accumulative method of liquid phase, for example powder metallurgy or reaction-injection moulding.

Claims (17)

1. be used for the rapid steel of saw blade, it is characterized in that, the alloying element composition of existence is made of following in mass percent: the carbon of 0.5-1.5; 1.0-10.0 chromium; 3.0-10.0 equivalent tungsten, this equivalence tungsten is provided by the 2Mo+W relational expression; 0.5-2.0 niobium, niobium can carry out partly or entirely substituting with the ratio of corresponding 2% niobium of per 1% vanadium with vanadium; 0.3-2.0 vanadium, vanadium can carry out partly or entirely substituting with the ratio of corresponding 2% niobium of per 1% vanadium with niobium; 0.3-3.5 silicon, silicon can carry out partly or entirely substituting with the ratio of 1:1 with aluminium; Be lower than 8 cobalt; All the other are unavoidable impurities in Fe and the preparation process substantially.
2. according to the rapid steel that is used for saw blade of claim 1, it is characterized in that the alloying element composition of existence is made of following substantially in mass percent: the carbon of 0.6-1.4; 3.0-7.0 chromium; 4.0-8.0 equivalent tungsten, this equivalence tungsten is provided by the 2Mo+W relational expression; 0.8-1.6 niobium, niobium can carry out partly or entirely substituting with the ratio of corresponding 2% niobium of per 1% vanadium with vanadium; 0.5-1.0 vanadium, vanadium can carry out partly or entirely substituting with the ratio of corresponding 2% niobium of per 1% vanadium with niobium; 0.7-2.0 silicon, silicon can carry out partly or entirely substituting with the ratio of 1:1 with aluminium; Be lower than 5 cobalt; All the other are unavoidable impurities in Fe and the preparation process substantially.
3. according to the rapid steel that is used for saw blade of claim 1, it is characterized in that the alloying element composition of existence is made of following substantially in mass percent: the carbon of 0.8-1.1; 3.0-5.0 chromium; 4.0-8.0 equivalent tungsten, this equivalence tungsten is provided by the 2Mo+W relational expression; 0.8-1.4 niobium, niobium can carry out partly or entirely substituting with the ratio of corresponding 2% niobium of per 1% vanadium with vanadium; 0.5-1.0 vanadium, vanadium can carry out partly or entirely substituting with the ratio of corresponding 2% niobium of per 1% vanadium with niobium; 0.7-1.5 silicon, silicon can carry out partly or entirely substituting with the ratio of 1:1 with aluminium; Be lower than 2 cobalt; All the other are unavoidable impurities in Fe and the preparation process substantially.
4. according to each the rapid steel that is used for saw blade in the claim 1 to 3, it is characterized in that, comprise the aluminium of 0.5-2.0% in mass percent.
5. according to each the rapid steel that is used for saw blade in the claim 1 to 3, it is characterized in that, comprise the aluminium of 0.8-1.2% in mass percent.
6. according to each the rapid steel that is used for saw blade in the claim 1 to 3, it is characterized in that, comprise maximum 1.5 manganese, maximum 1.0 aluminium, maximum 0.10 phosphorus, maximum 0.10 sulphur and maximum 0.10 nitrogen in mass percent.
7. according to each the rapid steel that is used for saw blade in the claim 1 to 6, it is characterized in that, comprise maximum 1.0 manganese, maximum 0.5 aluminium, maximum 0.08 phosphorus, maximum 0.01 sulphur and maximum 0.02 nitrogen in mass percent.
8. according to each the rapid steel that is used for saw blade in the claim 1 to 7, it is characterized in that, comprise in mass percent and be lower than 1 cobalt.
9. according to each the rapid steel that is used for saw blade in the claim 1 to 7, it is characterized in that, comprise maximum 0.5 manganese, maximum 0.2 aluminium, maximum 0.04 phosphorus, maximum 0.005 sulphur and maximum 0.01 nitrogen in mass percent.
10. according to each the rapid steel that is used for saw blade in the claim 1 to 9, it is characterized in that, comprise maximum 0.5 Ce or other rare earth element in mass percent, lanthanon in the periodictable or actinide elements, and La, Ac, Hf and Rf element are thought rare earth element.
11., it is characterized in that according to each the rapid steel that is used for saw blade in the claim 1 to 10, comprise titanium, zirconium or the tantalum element that partly or entirely substitutes niobium and v element in mass percent, wherein the pass of being complied with is the corresponding 1 part of vanadium of 1 part of Ti or 0.5 part of niobium; And 1 part of Ta or the corresponding 2 parts of vanadium of Zr or 1 part of niobium.
12., it is characterized in that this rapid steel is used for cutting tool and processing according to each the rapid steel that is used for saw blade in the claim 1 to 11.
13. according to each the rapid steel that is used for saw blade in the claim 1 to 11, it is characterized in that, this rapid steel is used for the saw blade of hand and machine or saw, and they are formed by rapid steel or the bimetal type fully, and the latter comprises the cutting tip of only being made by rapid steel.
14. according to each the rapid steel that is used for saw blade in the claim 1 to 11, it is characterized in that this rapid steel is used for rotary cutting, for example wimble, milling attachment, screwtap, screw plate and be used for processing metallic or other instrument of other material.
15., it is characterized in that this rapid steel is used to have the machining tool of low working life expection, for example poor efficiency industry instrument and household appliance according to each the rapid steel that is used for saw blade in the claim 1 to 11.
16., it is characterized in that this rapid steel is used for the process of cold shaping, warm shaping and hot shaping non-ferrous alloy or other solid material according to each the rapid steel that is used for saw blade in the claim 1 to 11.
17. according to each the rapid steel that is used for saw blade in the claim 1 to 11, it is characterized in that, this rapid steel forges, forges continuously by routine or comprises that alloy fragmentation and accumulative method make, what belong to them has powder metallurgy, powder injection and an injection shaping, about the finished product that obtain by hot shaping, for example be coiled material, bar, wire rod, sheet material and band, the product that directly uses perhaps or even under the rough forge condition.
CNA2007800143060A 2006-04-24 2007-02-02 High-speed steel for saw blades Pending CN101426944A (en)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
BRPI06016790 2006-04-24
BRPI0601679-0B1A BRPI0601679B1 (en) 2006-04-24 2006-04-24 FAST STEEL FOR SAW BLADES

Publications (1)

Publication Number Publication Date
CN101426944A true CN101426944A (en) 2009-05-06

Family

ID=38624481

Family Applications (1)

Application Number Title Priority Date Filing Date
CNA2007800143060A Pending CN101426944A (en) 2006-04-24 2007-02-02 High-speed steel for saw blades

Country Status (10)

Country Link
US (1) US20090123322A1 (en)
EP (1) EP2010688A4 (en)
JP (1) JP2009534536A (en)
KR (1) KR20080111101A (en)
CN (1) CN101426944A (en)
BR (1) BRPI0601679B1 (en)
MX (1) MX2008013467A (en)
RU (1) RU2440437C2 (en)
WO (1) WO2007121542A1 (en)
ZA (1) ZA200809962B (en)

Cited By (12)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN101748334B (en) * 2010-01-08 2011-05-04 北京工业大学 High hardness cast boron-containing low alloy wear-resistant high-speed steel and preparation method thereof
CN102732796A (en) * 2012-06-07 2012-10-17 江苏天工工具有限公司 High-performance high-speed steel
CN103586458A (en) * 2013-11-09 2014-02-19 马鞍山成宏机械制造有限公司 Powder metallurgy tool with good toughness and high hardness and preparation method thereof
CN104250709A (en) * 2013-06-28 2014-12-31 江苏天工工具有限公司 High quality TG42 saw blade high speed steel
CN104532134A (en) * 2014-12-18 2015-04-22 无锡伊诺永利文化创意有限公司 High-speed steel
CN105579604A (en) * 2013-09-27 2016-05-11 日立金属株式会社 High-speed-tool steel and method for producing same
CN106399645A (en) * 2016-12-09 2017-02-15 大连圣洁真空技术开发有限公司开发区分公司 CFW composite high-speed steel quenching process
CN106425350A (en) * 2016-12-23 2017-02-22 诺鑫（南通）医疗技术有限公司 Preparation method of medical power reciprocating saw blade
CN107217213A (en) * 2017-04-14 2017-09-29 江苏羽立新材料科技有限公司 A kind of superhard lathe tool low-phosphorous sulphur high-ductility rare earth alloy material and its preparation technology
CN112041469A (en) * 2018-04-11 2020-12-04 Qsgs技术格拉季娜克莱普塞夫斯卡公司 Steel for single-piece band saw and double-metal band saw for wood
CN114713796A (en) * 2022-05-06 2022-07-08 湖南三泰新材料股份有限公司 Hot-rolled powder high-speed steel and preparation method thereof
CN117230385A (en) * 2023-10-16 2023-12-15 河北炳岩新材科技有限公司 Low-cost M35 high-speed steel wire rod and preparation method thereof

Families Citing this family (11)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
BRPI0603856A (en) * 2006-08-28 2008-04-15 Villares Metals Sa hard alloys of lean composition
IT1401998B1 (en) * 2010-09-30 2013-08-28 Danieli Off Mecc CUTTING SHEET OF LAMINATED PRODUCTS AND ITS PRODUCTION PROCESS
KR101925275B1 (en) * 2011-03-25 2018-12-06 닛신 세이코 가부시키가이샤 Steel plate with excellent durability for band-shaped die-cutting blade, and band-shaped die-cutting blade
DE202013012601U1 (en) * 2013-07-03 2017-11-28 J. D. Theile Gmbh & Co. Kg Chain link for mining applications
KR101826488B1 (en) * 2015-03-26 2018-02-06 히타치 긴조쿠 가부시키가이샤 Cold work tool and method for manufacturing same
CN105603319B (en) * 2016-01-01 2017-11-14 衢州市联橙环保科技有限公司 A kind of rubbish from cooking breaker
JP2017155310A (en) * 2016-03-03 2017-09-07 日新製鋼株式会社 Handsaw
CN108044188A (en) * 2017-12-22 2018-05-18 湖北大帆金属制品有限公司 A kind of 65Mn circular saw bits processing technology
CN113913689A (en) * 2021-09-18 2022-01-11 天工爱和特钢有限公司 Jet high-speed steel without annular segregation and with secondary hardening and manufacturing method thereof
CN114015926A (en) * 2021-11-10 2022-02-08 河冶科技股份有限公司 Preparation method of high-V high-speed steel and high-V high-speed steel
US20240183014A1 (en) * 2022-12-03 2024-06-06 Arthur Craig Reardon High Speed Steel Composition

Family Cites Families (14)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4168159A (en) * 1978-02-28 1979-09-18 Latrobe Steel Company High speed steels with phosphorus for improved cutting performance
SE8106207L (en) * 1980-11-10 1982-05-11 Teledyne Ind SPEEDS AND OTHER TOOLS
JPS5785952A (en) * 1980-11-17 1982-05-28 Daido Steel Co Ltd High-speed steel
PL256701A1 (en) * 1985-12-06 1987-09-21 Akad Gorniczo Hutnicza Alloyed tool steel of high resistance to abrasive wear
JPH07116550B2 (en) * 1987-09-24 1995-12-13 日立金属株式会社 Low alloy high speed tool steel and manufacturing method thereof
WO1993002821A1 (en) * 1991-08-07 1993-02-18 Kloster Speedsteel Aktiebolag High-speed steel manufactured by powder metallurgy
AU2405192A (en) * 1991-08-07 1993-03-02 Kloster Speedsteel Aktiebolag High-speel manufactured by powder metallurgy
SE508872C2 (en) * 1997-03-11 1998-11-09 Erasteel Kloster Ab Powder metallurgically made steel for tools, tools made therefrom, process for making steel and tools and use of steel
JPH10330894A (en) * 1997-06-05 1998-12-15 Daido Steel Co Ltd Low alloy high speed tool steel and its production
ATE206485T1 (en) * 1998-01-06 2001-10-15 Sanyo Special Steel Co Ltd THE PRODUCTION OF COLD WORK TOOL STEEL
SE512970C2 (en) * 1998-10-30 2000-06-12 Erasteel Kloster Ab Steel, the use of the steel, the product made of the steel and the way of making the steel
JP2004169177A (en) * 2002-11-06 2004-06-17 Daido Steel Co Ltd Alloy tool steel, its manufacturing method, and die using it
JP2004285444A (en) * 2003-03-24 2004-10-14 Daido Steel Co Ltd Low-alloy high-speed tool steel showing stable toughness
BRPI0603856A (en) * 2006-08-28 2008-04-15 Villares Metals Sa hard alloys of lean composition

Cited By (14)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN101748334B (en) * 2010-01-08 2011-05-04 北京工业大学 High hardness cast boron-containing low alloy wear-resistant high-speed steel and preparation method thereof
CN102732796A (en) * 2012-06-07 2012-10-17 江苏天工工具有限公司 High-performance high-speed steel
CN104250709A (en) * 2013-06-28 2014-12-31 江苏天工工具有限公司 High quality TG42 saw blade high speed steel
CN105579604A (en) * 2013-09-27 2016-05-11 日立金属株式会社 High-speed-tool steel and method for producing same
CN103586458B (en) * 2013-11-09 2016-01-06 马鞍山成宏机械制造有限公司 Powder metallurgy tool that a kind of toughness strong hardness is large and preparation method thereof
CN103586458A (en) * 2013-11-09 2014-02-19 马鞍山成宏机械制造有限公司 Powder metallurgy tool with good toughness and high hardness and preparation method thereof
CN104532134A (en) * 2014-12-18 2015-04-22 无锡伊诺永利文化创意有限公司 High-speed steel
CN106399645A (en) * 2016-12-09 2017-02-15 大连圣洁真空技术开发有限公司开发区分公司 CFW composite high-speed steel quenching process
CN106425350A (en) * 2016-12-23 2017-02-22 诺鑫（南通）医疗技术有限公司 Preparation method of medical power reciprocating saw blade
CN107217213A (en) * 2017-04-14 2017-09-29 江苏羽立新材料科技有限公司 A kind of superhard lathe tool low-phosphorous sulphur high-ductility rare earth alloy material and its preparation technology
CN112041469A (en) * 2018-04-11 2020-12-04 Qsgs技术格拉季娜克莱普塞夫斯卡公司 Steel for single-piece band saw and double-metal band saw for wood
CN114713796A (en) * 2022-05-06 2022-07-08 湖南三泰新材料股份有限公司 Hot-rolled powder high-speed steel and preparation method thereof
CN114713796B (en) * 2022-05-06 2024-04-19 湖南三泰新材料股份有限公司 Hot-rolled powder high-speed steel and preparation method thereof
CN117230385A (en) * 2023-10-16 2023-12-15 河北炳岩新材科技有限公司 Low-cost M35 high-speed steel wire rod and preparation method thereof

Also Published As

Publication number Publication date
MX2008013467A (en) 2009-02-11
US20090123322A1 (en) 2009-05-14
KR20080111101A (en) 2008-12-22
BRPI0601679A (en) 2007-12-18
WO2007121542A1 (en) 2007-11-01
RU2008146047A (en) 2010-05-27
JP2009534536A (en) 2009-09-24
BRPI0601679B1 (en) 2014-11-11
RU2440437C2 (en) 2012-01-20
EP2010688A1 (en) 2009-01-07
ZA200809962B (en) 2009-11-25
EP2010688A4 (en) 2010-08-04

Similar Documents

Publication Publication Date Title
CN101426944A (en) High-speed steel for saw blades
US20220119927A1 (en) Wear resistant alloy
CN101528971B (en) Hard alloys with dry composition
EP1236809B1 (en) High-hardness martensitic stainless steel excellent in corrosion resistance
CN100540712C (en) The martensitic precipitation hardening stainless steel
CA2659303A1 (en) Steel alloy, a holder or a holder detail for a plastic moulding tool, a tough hardened blank for a holder or holder detail, a process for producing a steel alloy
EP1910583A1 (en) Corrosion-resistant, cold-formable, machinable, high strength, martensitic stainless steel
CN109563579A (en) Steel for high-frequency quenching
CN103097562A (en) Steel for extrusion tools
EP3034211A1 (en) A wear resistant tool steel produced by HIP
CN109477180A (en) Steel for high-frequency quenching
EP2681340B1 (en) Hot-work tool steel and a process for making a hot-work tool steel
JP2002535496A (en) Hard tool steels and powder metallurgy steels therefrom
CA2381236C (en) Steel material, its use and its manufacture
WO2018056884A1 (en) Hot work tool steel
JP2004515654A (en) Steel alloys, holders and holder parts for plastic molding tools, and tough-hardened blanks for holders and holder parts
JP2005187900A (en) Cold tool steel having excellent surface treatability, component for die, and die
EP3132066B1 (en) Cold work tool steel
JPH09165649A (en) Hot tool steel excellent in high temperature strength and fracture toughness
CN104640654A (en) Method for cutting cold work tool steel, and method for producing cold-working die material
JPH09227990A (en) Hot tool steel excellent in high temperature strength and fracture toughness
EP2896714B1 (en) Creping blade and method for its manufacturing
CN102102164B (en) Metal mould steel with excellent thermal machinability
JPH1161331A (en) Hot tool steel
JPH09291346A (en) High toughness material excellent in wear resistance in rust generating environment

Legal Events

Date Code Title Description
C06 Publication
PB01 Publication
C10 Entry into substantive examination
SE01 Entry into force of request for substantive examination
REG Reference to a national code

Ref country code: HK

Ref legal event code: DE

Ref document number: 1132304

Country of ref document: HK

C02 Deemed withdrawal of patent application after publication (patent law 2001)
WD01 Invention patent application deemed withdrawn after publication

Application publication date: 20090506

REG Reference to a national code

Ref country code: HK

Ref legal event code: WD

Ref document number: 1132304

Country of ref document: HK