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CN1263880C - High strength stainless steel wire excellent in ductility-toughness and modulus of rigidity and method for production thereof - Google Patents

High strength stainless steel wire excellent in ductility-toughness and modulus of rigidity and method for production thereof Download PDF

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Publication number
CN1263880C
CN1263880C CNB02813737XA CN02813737A CN1263880C CN 1263880 C CN1263880 C CN 1263880C CN B02813737X A CNB02813737X A CN B02813737XA CN 02813737 A CN02813737 A CN 02813737A CN 1263880 C CN1263880 C CN 1263880C
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Prior art keywords
wire
hand
steel wire
steel
drawn wire
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CN1526032A (en
Inventor
高野光司
竹内和久
多田好宣
谷本好则
秋月孝之
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Nippon Seisen Co Ltd
Nippon Stainless Steel Co Ltd
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Nippon Seisen Co Ltd
Nippon Steel Corp
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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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
    • B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
    • B23K35/24—Selection of soldering or welding materials proper
    • B23K35/26—Selection of soldering or welding materials proper with the principal constituent melting at less than 400 degrees C
    • B23K35/262—Sn as the principal constituent
    • 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
    • C21D7/00—Modifying the physical properties of iron or steel by deformation
    • C21D7/02—Modifying the physical properties of iron or steel by deformation by cold working
    • C21D7/10—Modifying the physical properties of iron or steel by deformation by cold working of the whole cross-section, e.g. of concrete reinforcing bars
    • 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
    • C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
    • C21D8/065—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires 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
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • C21D9/525—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length for wire, for rods
    • 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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • 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
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K2101/00—Articles made by soldering, welding or cutting
    • B23K2101/36—Electric or electronic devices
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Manufacturing & Machinery (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Strip Materials And Filament Materials (AREA)
  • Metal Extraction Processes (AREA)

Abstract

本发明提供了规定基本成分和氧、硫，使用晶粒微细化和由冷拔丝加工的奥氏体形变热处理的强韧化效果，显著提高延韧性和刚性模量的高强度不锈钢钢丝及其制造方法，该钢丝以质量%计，含有C：0.03～0.14%、Si：0.1～4.0%、Mn：0.1～5.0%、Ni：5.0～9.0%、Cr：14.0～19.0%、N：0.005～0.20%、O：0.001～0.01%、S：0.0001～0.012%，其余由Fe和不可避免的杂质构成，并且，2C+N为0.17～0.32%，下述式(1)的Ni当量(%)的值为20～24，H4ppm。Ni当量(%)＝Ni+0.65Cr+0.98Mo+1.06Mn+0.35Si+12.6(C+)(1)。The present invention provides a high-strength stainless steel wire with specified basic components, oxygen and sulfur, using the strengthening and toughening effect of grain refinement and austenite deformation heat treatment processed by cold drawing, and significantly improving ductility, toughness and rigid modulus and its production Method, the steel wire contains C: 0.03-0.14%, Si: 0.1-4.0%, Mn: 0.1-5.0%, Ni: 5.0-9.0%, Cr: 14.0-19.0%, N: 0.005-0.20% in mass % %, O: 0.001-0.01%, S: 0.0001-0.012%, the rest is composed of Fe and unavoidable impurities, and 2C+N is 0.17-0.32%, the Ni equivalent (%) of the following formula (1) The value is 20-24, H4ppm. Ni equivalent (%)=Ni+0.65Cr+0.98Mo+1.06Mn+0.35Si+12.6(C+) (1).

Description

High-strength stainless steel steel wire and manufacture method thereof that the number of torsions rigidity modulus is good
Technical field
The present invention relates to the high-strength stainless steel steel wire, in more detail, the hand-drawn wire processing of passing through that relates to high strength austenite stainless steel steel wire improves the technology of prolonging toughness (ductility, toughness) and rigidity modulus.
Background technology
Always, spring high strength stainless steel steel wire such as is used to exist hand-drawn wire to add and is produced lobe (aging crack) problem man-hour, so proposed its predetermined component, hydrogen amount and hot candied processing back strain are caused the technology (spy open flat 10-121208) of living martensite volume to prevent this problem.
In addition,, for a long time, in carbon steel, studied the processing back under hot or warm state, austenite structure has been carried out cooling transformation become martensitic ausforming heat-treating methods about the toughening technology (the toughness technology is prolonged in improvement) of ferrous materials.(for example, Japanese Metallkunde can be reported No. the 8th, the 27th volume,, p623～639 in 1988).But this method must be quenched behind hot temperature or warm temperature province processing austenite structure immediately, therefore is subjected to bigger restriction, does not almost popularize industrial.
In the prior art, the strategy that prolongs toughness (ductility and toughness) and rigidity modulus that raising is used for the stainless steel steel wire that spring uses etc. did not carry out research.Particularly as steel wire for high strength spring prolong the flexible index, number of torsions is important.
In the use of high-strength stainless steel spring, from prevent the accident of losing and improve spring constant and make it to stablize, light-weighted viewpoint, improve the high-strength stainless steel steel wire prolong toughness (number of torsions) and rigidity modulus becomes most important problem.
Thereby, the objective of the invention is to, provide a kind of except regulation basal component and purity (oxygen, sulphur), the heat treated highly malleablized effect of ausforming of utilizing the crystal grain miniaturization and being caused by hand-drawn wire processing improves significantly and prolongs toughness and rigidity modulus ground high-strength stainless steel steel wire and manufacture method thereof.
Summary of the invention
The inventor has carried out all research for solving above-mentioned problem, found that, in austenite stainless steel, except the basal component and purity (oxygen, sulphur) of regulation parent metal, limit tissue, intensity and hand-drawn wire processing conditions, utilize the heat treated highly malleablized effect of crystal grain miniaturization and ausforming, the high-strength stainless steel steel wire that can stably be significantly improved and prolong toughness and rigidity modulus.The present invention finishes with regard to being based on such discovery.
That is, main points of the present invention are as described below.
The present invention is the good high-strength stainless steel steel wire of number of torsions rigidity modulus, it is characterized in that, in quality %, contain C:0.03～0.14%, Si:0.1～4.0%, Mn:0.1～5.0%, Ni:5.0～9.0%, Cr:14.0～19.0%, N:0.005～0.20%, 0:0.001～0.01%, S:0.0001～0.012%, and then contain following A, B's is wantonly more than a kind or a kind, and contain C as required, all the other are made of Fe and unavoidable impurities, and, 2C+N is 0.17～0.32%, the value of the Ni equivalent (%) of following formula (1) is 20～24, H≤4ppm
A:Al, Nb, Ti, Zr, Ta, W's is wantonly more than a kind or a kind, is respectively 0.01～0.30%;
B:V is 0.1～0.5%;
C:Mo is 0.2～3.0%;
Ni equivalent (quality %)=Ni+0.65Cr+0.98Mo+1.06Mn+0.35Si+12.6 (C+N)
(1)
In addition, the value of the GI of the preferred following formula of above-mentioned steel wire of the present invention (2) is below 30 or 30.
GI(％)＝16C+2Mn+9Ni-3Cr+8Mo+15N (2)
In addition, the present invention is the manufacture method of the good high-strength stainless steel steel wire of number of torsions rigidity modulus, this method is for will be in quality %, contain C:0.03～0.14%, Si:0.1～4.0%, Mn:0.1～5.0%, Ni:5.0～9.0%, Cr:14.0～19.0%, N:0.005～0.20%, O:0.001～0.01%, S:0.0001～0.012%, all the other are made of Fe and unavoidable impurities, and, 2C+N is 0.17～0.32%, the value of the Ni equivalent (%) of following formula (1) is after 20～24 steel carries out hot rolling and makes wire rod and carry out solution treatment, this wire rod is carried out after solution treatment more than 1 time or 1 time and hand-drawn wire be processed into crin, implementing cold precision work makes in the series of processes of steel wire, at least in the atmosphere of hydrogen not, carry out last solution treatment, making H in the steel is 4ppm or below the 4ppm, carries out cold accurately machined hot candied processing according to the hot candied amount of finish ε with formula (3) expression in the scope of formula (4).
Ni equivalent (%)=Ni+0.65Cr+0.98Mo+1.06Mn+0.35Si+12.6 (C+N)
(1)
ε＝ln(A 0/A) (3)
Wherein, A 0: the wire rod before the hand-drawn wire processing or the basal area of crin
A: the basal area of the steel wire after the hand-drawn wire processing
0.15 * (Ni equivalent)-2.28≤ε≤0.15 * (Ni equivalent)-0.88 (4)
In addition, above-mentioned manufacture method of the present invention is preferably in aforementioned a series of operation, additional operation prior to the solution treatment carried out in the atmosphere of hydrogen not, in this additional process, in 200 ℃～600 ℃ atmosphere of hydrogen not, implement dehydrogenation and handle.
In addition, in manufacture method of the present invention, above-mentioned steel, wire rod or crin can also contain in quality %, be selected among following A, B, the C any or more than.
A:Al, Nb, Ti, Zr, Ta, W's is wantonly more than a kind or a kind, is respectively 0.01～0.30%
B:V is 0.1～0.5%
C:Mo is 0.2～3.0%
In addition, in manufacture method of the present invention, preferably making austenite average crystal grain diameter before the hand-drawn wire processing of above-mentioned wire rod or crin is 30 μ m or below the 30 μ m.
Embodiment
At first narrate the composition range of stainless steel steel wire of the present invention.In addition, in the following description, only otherwise specify in advance, % is whole expression quality % just.
In order to obtain the high strength after hand-drawn wire is processed with N, add the C more than 0.03% or 0.03%.But, when surpassing 0.14% interpolation, on crystal boundary, separate out the Cr carbide, can reduce and prolong toughness, thereby will be defined as 0.14% on it.
For deoxidation, add the Si more than 0.1% or 0.1%.But when surpassing 4.0% interpolation, not only its effect is saturated, and manufacturing is poor, in addition, owing to prolong the toughness variation on the contrary, and so will be defined as 4.0% on it.
For deoxidation with in order to adjust the Ni equivalent, add the Mn more than 0.1% or 0.1%.But when surpassing 5.0% interpolation, rigidity modulus reduces, thereby will be defined as 5.0% on it.
In order to ensure prolonging toughness and adjusting the Ni equivalent, add the Ni more than 5.0% or 5.0%.But when surpassing 9.0% interpolation, rigidity modulus reduces, thereby will be defined as 5.0% on it.
In order to ensure erosion resistance and adjustment Ni equivalent, add the Cr more than 14.0% or 14.0%.But, when surpassing 19.0% interpolation, prolong the toughness deterioration, thereby will be defined as 19.0% on it.
In order to obtain the high strength after hand-drawn wire is processed with C, add the N more than 0.005% or 0.005%.But, when surpassing 0.20% interpolation, can generate pore during manufacturing, the remarkable variation of manufacturing, thereby will be defined as 0.20% on it.
In order to ensure number of torsions, regulation 0 is below 0.01% or 0.01%.But, if be controlled at 0.001% or 0.001% when following, industrial cost up, the cost/performance ratio variation, thereby will be defined as 0.001% under it.
In order to ensure number of torsions, limiting S is below 0.012% or 0.012%.But, if be controlled at 0.0001% or 0.0001% when following, industrial cost up, the cost/performance ratio variation, thereby will be defined as 0.0001% under it.
In order to ensure prolonging toughness, the hydrogen in the steel is decided to be 4ppm or below the 4ppm.Particularly preferably in 1.5ppm or below the 1.5ppm.
Al, Nb, Ti, Zr, Ta, W can form fine carbonitride, make the austenite crystal miniaturization stably after the solution treatment of steel wire, improve and prolong toughness, thereby add wantonly more than a kind or a kind more than 0.01% or 0.01% as required respectively.But, adding 0.30% or 0.30% when above, its effect is saturated; Not only uneconomical, prolong toughness on the contrary and reduce, thereby will be defined as 0.30% on it.
Particularly Al and Nb when improving hot workability, help high strength by precipitating reinforcing effect, so effectively.
V and Al, Nb, Ti, Zr, Ta, W can form fine carbonitride equally, make the austenite crystal miniaturization stably after the solution treatment of steel wire, have improved and have prolonged toughness, thereby added as required more than 0.1% or 0.1%.But, adding 0.5% or 0.5% when above, its effect is saturated, prolongs the toughness reduction on the contrary, thereby will be defined as 0.5% on it.
Mo is effective to erosion resistance, thereby adds as required more than 0.2% or 0.2%.But when surpassing 3.0% interpolation, its effect is saturated, and opposite Young's modulus reduces, thereby will be defined as 3.0% on it.Especially preferably be taken as below 2.0% or 2.0%.
Cu can suppress the work hardening of austenite structure, reduces the intensity of the steel wire after hand-drawn wire is processed, thereby as required, preferably is reduced to below 0.8% or 0.8%.
P makes to prolong the element that toughness reduces, thereby as required, preferably it is reduced to below 0.02% or 0.02%.
Below the intensity and the strain of the steel wire after the processing of explanation hand-drawn wire cause living martensitic amount.
The tensile strength of the steel wire after the hand-drawn wire processing is lower than 1700N/mm 2Occasion owing to be to prolong the toughness height basically, so can not manifest effect of the present invention significantly.Relative therewith, the tensile strength of the steel wire after the hand-drawn wire processing becomes 1700N/mm 2Or 1700N/mm 2During above high strength material, reduce owing to prolong toughness, so just can make the effect of the present invention of crystal grain miniaturization and ausforming thermal treatment etc. clear and definite.Thereby the tensile strength of the steel wire after preferably hand-drawn wire being processed is defined as 1700N/m 2Or 1700N/mm 2More than.Be preferably 1900N/mm especially 2Or 1900N/mm 2More than, but higher limit is decided to be 2800N/mm 2For good.
In addition, the strain of the steel wire after the hand-drawn wire processing causes living martensite volume and is lower than 20% occasion, and the tensile strength of the steel wire after the hand-drawn wire processing can be lower than 1700N/mm usually 2, can not manifest height of the present invention significantly and prolong the flexible effect, in addition, rigidity modulus is step-down also.Therefore preferred strain causes living martensite volume more than 20% or 20%.On the other hand, the strain after the hand-drawn wire processing causes living martensite volume and surpasses at 80% o'clock, and the heat treated tough martensite volume of ausforming itself can reduce, and prolongs toughness and reduces.Therefore, preferably will on be defined as 80%.Particularly in order to bring into play highly malleablized and the high rigidity modulus that is produced by ausforming thermal treatment to greatest extent, the strain of the steel wire after preferably hand-drawn wire being processed causes living martensite volume and is defined as 40%～70%.
In addition, this strain causes the mensuration of living martensite volume (volume %), for example can be with being obtained by the saturation magnetic flux density of the mensuration such as determinator of dc magnetizing characteristic.In addition, must revise with the silk footpath with the occasion of mensuration such as easy ferrite instrument (Off エ ラ イ ト メ one ).
2C+N amount (%) and formula (1), the formula (2) of regulation in the present invention below are described.
2C+N (%) is that the result of the effects of tensile strength of the steel wire after by investigation C, N hand-drawn wire being processed obtains.In order to ensure the tensile strength of the steel wire after the hand-drawn wire processing at 1700N/mm 2Or 1700N/mm 2More than, just 2C+N is limited to 0.17 (%) or more than 0.17 (%).But, when surpassing 0.32 (%), reduce owing to prolong toughness, thus will on be defined as 0.32 (%).Particularly from stable high strength (tensile strength 〉=1900N/mm 2) and height prolong the flexible viewpoint and set out, preferably in 0.20 (%)～0.30 (%).
In addition, the Ni equivalent of formula (1) is that the result who prolongs the flexible influence of the steel wire after each element of investigation is processed hand-drawn wire draws, and is that the expression effective element is to prolonging the flexible influence degree.
Ni equivalent (%)=Ni+0.65Cr+0.98Mo+1.06Mn+0.35Si+12.6 (C+N)
(1)
When the Ni equivalent value surpassed 24 (%), the strain of the steel wire after the hand-drawn wire processing caused living martensite volume and reduces, and intensity reduces, and effect of the present invention weakens, so be decided to be 24 (%) or more than 24 (%).On the other hand, when the normal value of Ni was lower than 20 (%), the heat treated martensite of ausforming of the steel wire after the hand-drawn wire processing itself can reduce, and prolonged toughness and reduced, thereby will be defined as 20% down.Particularly, preferably the Ni equivalent is decided to be 21 (%)～23 (%) in order to maximally utilise the heat treated highly malleablized of ausforming by common hand-drawn wire processing.
In addition, the GI (%) of formula (2) be by each element of investigation to the obtaining of the result of the influence of the rigidity modulus after the hand-drawn wire processing, be that expression is to rigidity modulus effective elements and influence degree.
GI(％)＝16C+2Mn+9Ni-3Cr+8Mo+15N (2)
As required the value of GI is decided to be 30 (%) or below 30 (%).When the value of GI surpasses 30 (%), because the rigidity modulus after the hand-drawn wire processing is low, so preferably will be defined as 30 (%) on it.Especially preferably be decided to be 25 (%) or below 25 (%).
The manufacturing process of steel wire of the present invention below summarily is described.
Steel wire of the present invention can with following 1., 2. arbitrary operation manufacturing.
Promptly, want the steel of composition to carry out hot rolling with adjusting to and make stainless steel wire rod, and after making its solution treatment (also comprise rolling after continuous processing), 1. make steel wire (end article) with the processing of precision work hand-drawn wire, or the 2. occasion that differs greatly of final steel filament diameter and stainless steel wire rod diameter, make the stainless steel wire rod processing of the hand-drawn wire more than 1 time or 1 time repeatedly, the annealing (solution treatment) of above-mentioned solution treatment, make crin (line), after this crin implemented many continuous annealings (solution treatment), implement the processing of precision work hand-drawn wire and make steel wire (end article).In this series of processes, solution treatment (comprising many continuous annealings) is no matter in containing the atmosphere of hydrogen or do not contain that carry out in the atmosphere of hydrogen can, but, as aftermentioned of the present invention, at least last solution treatment, in the atmosphere that does not contain hydrogen, carry out, carry out the processing of precision work hand-drawn wire under given conditions.In addition, said here solution treatment is to instigate carbide to become solid solution condition.
In addition, in the present invention,, in the atmosphere that does not contain hydrogen, carry out dehydrogenation and handle, carry out the processing of precision work hand-drawn wire under given conditions as an operation in the above-mentioned series of processes.
Below, the condition that hand-drawn wire is processed describes.
The wire rod after formula (3) the expression solution treatment or the hand-drawn wire amount of finish of crin, formula (4) is represented its scope.
ε＝ln(A 0/A) (3)
Wherein, A 0: the wire rod before the hand-drawn wire processing or the basal area of crin
A: the basal area of the steel wire after the hand-drawn wire processing
0.15 * (Ni equivalent)-2.28≤ε≤0.15 * (Ni equivalent)-0.88 (4)
At room temperature implement the occasion of general hand-drawn wire processing, fall in the scope of stipulating with formula (4) with the value of the hand-drawn wire amount of finish ε of formula (3) regulation.Than the littler occasion of scope of formula (4), the tensile strength of the steel wire after the hand-drawn wire processing reduces, in addition also step-down of rigidity modulus.On the other hand, than the bigger occasion of scope of formula (4), the martensite volume of the steel wire after the hand-drawn wire processing increases, and prolongs toughness and reduces.Therefore, limit the hand-drawn wire amount of finish after the solution treatment with formula (3), formula (4).
The solution treatment (comprising many continuous annealings) of wire rod or crin and the condition that dehydrogenation is handled below are described.
As previously mentioned, the hydrogen amount of prolonging in toughness and the steel wire demonstrates interdependence.When carrying out solution treatment in the atmosphere of the reducing gas that contains hydrogen, because of absorbing hydrogen, steel can contain the hydrogen above 4ppm, prolongs the toughness variation.Therefore, under atmosphere such as the argon gas that does not contain hydrogen, nitrogen, atmosphere, carry out during last at least solution treatment in the above-mentioned operation, make in the steel content of hydrogen become 4ppm or below the 4ppm.Particularly preferably in carrying out under the atmosphere such as argon gas, to prevent surface oxidation.
In addition, in order to make hydrogen amount in the steel become 4ppm or below the 4ppm, as an operation in the above-mentioned series of processes, for example, in the front and back of the solution treatment of the front and back of wire rod solution treatment, the front and back of solution treatment of hand-drawn wire processing of making crin or the processing of precision work hand-drawn wire etc., implement dehydrogenation and handle.That is, handle, then can improve and prolong toughness if in 200～600 ℃ the atmosphere that does not contain hydrogen, implement dehydrogenation.At this moment, below 200 ℃ or 200 ℃ the time, its effect is indeterminate, when surpassing 600 ℃, and iron scale thickening, manufacturing variation.Therefore preferably 200～600 ℃, more preferably under atmosphere such as 200～400 ℃ the argon gas that does not contain hydrogen, nitrogen, atmosphere, carry out dehydrogenation and handle.
The crystal grain diameter of the austenite structure before below the hand-drawn wire of explanation wire rod or crin is processed.
The average crystal grain diameter of the wire rod before the hand-drawn wire processing or the austenite structure of crin surpasses the occasion of 30 μ m, and the toughness of prolonging of the steel wire after the hand-drawn wire processing reduces.Therefore, as required, adjust the preceding wire rod of hand-drawn wire processing or the solution treatment condition of crin, for example be chilled to below 500 ℃ or 500 ℃ in order to the temperature range of average speed of cooling more than 5 ℃/second or 5 ℃/second from 950 ℃～1150 ℃, the average crystal grain diameter that makes austenite structure is at 30 μ m or below the 30 μ m.
Embodiment
Below further specifically describe the present invention based on embodiments of the invention.
The present invention, particularly as the target property of the steel wire after the hand-drawn wire processing, its tensile strength is at 1700N/mm 2Or 1700N/mm 2More than, the number of torsions that prolongs the flexible important factor of spring steel wire is more than 10 times or 10 times, the rigidity modulus of the important factor of the Young's modulus of spring steel wire is at 63GPa or more than the 63GPa.Important factor as Young's modulus also has Young's modulus, but stipulates as its typical value with rigidity modulus in the present invention.
The material that is for experiment of embodiment is in the manufacturing process of common STAINLESS STEEL WIRE, carries out melting, rolling until Φ 5.5mm and obtain 1000 ℃ of following finish to gauges at the hot wire rod that down carries out.The wire rod that obtains is implemented 1050 ℃, 5 minutes thermal treatment (solution treatment), and carry out water-cooled.Then, a part is implemented dehydrogenation and is handled, and makes the crin of intermediary hand-drawn wire processing.After this crin being implemented 1050 ℃ solution treatment under the argon gas atmosphere in many continuous annealing furnaces, implement the processing of precision work hand-drawn wire and make steel wire thereafter.
And austenitic average crystal grain diameter and precision work hand-drawn wire processing hydrogen amount, the strain of steel wire afterwards of investigating the crin of this precision work hand-drawn wire processing preceding (after the solution treatment) cause living martensite volume, tensile strength, number of torsions, rigidity modulus.
Electrolytic corrosion is carried out in the transverse section of crin in 10% salpeter solution, obtain each basal area of each crystallization with image analysis then, with the mean value of 10 points of the conversion diameter (d) of this area that converts, the austenitic average crystal grain diameter of the crin before the processing of expression hand-drawn wire.
From the steel wire after the hand-drawn wire processing, extract sample, measure the hydrogen amount with rare gas element fusion-thermal conduction assay method.
Measure saturation magnetization with single flow BH tracer, the strain of obtaining the steel wire after the precision work hand-drawn wire is processed causes living martensite volume.
Tensile strength with the steel wire after the stretching test measurement hand-drawn wire processing of JIS Z2241.
With the number of torsions that carries out the steel wire of twisting test after the number of torsions of fracture is estimated hand-drawn wire processing.
Measure the rigidity modulus of the steel wire after hand-drawn wire is processed with reversing arrangement.
At first narrate the effect of basal component of the present invention.Get the following steel wire that makes like that for test materials: will hotly carry out wire rod after the rolling and enforcement solution treatment of wire rod down and apply the intermediary hand-drawn wire and be processed into the crin of Φ 3.4mm, then under argon gas atmosphere, implement solution treatment, implement the precision work hand-drawn wire until Φ 1.6mm thereafter.Table 1 shows the basal component of embodiment and the characteristic of steel wire.
The present invention example No.1～No.19 and comparative example No.20～No.32 have been investigated matrix composition C, Si, Mn, P, S, Ni, Cr, Mo, Cu, O, the N influence to each characteristic of steel wire.
The tensile strength of whole steel wires of example of the present invention is at 1700N/mm 2Or 1700N/mm 2More than, number of torsions more than 10 times or 10 times, rigidity modulus is at 63Gpa or more than the 63Gpa, number of torsions and rigidity modulus are good under high strength.In addition, No.1 of the present invention and No.19 compare, and reduce because of making P, have improved number of torsions.
But in comparative example No.20, the C amount is low, though number of torsions and Young's modulus are not low, because of intensity is low, so effect of the present invention and not obvious.
In comparative example No.21, C measures high, and number of torsions is low.
In comparative example No.22, N measures high, because faults in material such as generation pore, so number of torsions is low.
In comparative example No.23, Si measures high, and number of torsions is low.
In comparative example No.24, Mn measures high, and number of torsions is low.
In comparative example No.25, Ni measures high, and it is low that strain causes living martensite volume, and rigidity modulus is poor.
In comparative example No.26, the Ni amount is low, and strain causes living martensite volume height, and number of torsions is low.
In comparative example No.27, the Cr amount is low, and strain causes living martensite volume height, and number of torsions is low.
In comparative example No.28, it is high that Cr measures, and not only number of torsions is low, and strain to cause living martensite volume also low, rigidity modulus is also poor.
In comparative example No.29, Mo measures high, and rigidity modulus is poor.
In comparative example No.30, it is high that Cu measures because tensile strength is low, so not only the effect of high number of torsions of the present invention is indeterminate, and strain to cause living martensite volume also low, rigidity modulus is also poor.
In comparative example No.31 and No.32, O amount and S amount are high respectively, and number of torsions is low.
Then, the effect of narrating crystal grain miniaturization of the present invention and adding crystal grain miniaturization element.Get the following steel wire that makes like that for test materials: will hotly carry out wire rod after the rolling and enforcement solution treatment of wire rod down and apply the intermediary hand-drawn wire and be processed into the crin of Φ 3.4mm, then under argon gas atmosphere, implement solution treatment, implement the precision work hand-drawn wire until Φ 1.6mm thereafter.。Table 2 shows the basal component of embodiment and the characteristic of steel wire.
The present invention example No.33～No.44 and comparative example No.45, No.46 have been investigated the crystal grain miniaturization and added the effect of crystal grain miniaturization element to the number of torsions of steel wire.
In the present invention's example No.34～No.44, for the crystal grain miniaturization, added Al, Nb, Ti, Zr, Ta, W, V, average crystal grain diameter becomes 10 μ m, and No.33 compares with the present invention's example, and number of torsions further improves significantly.Shown the effect of crystal grain miniaturization to high number of torsions.In addition, with the tensile strength among the present invention of table 2 example No.34～No.44 (the Ni equivalent all is 21.7～22.1%) at 2000N/mm 2Or 2000N/mm 2Above No.35,36,38,44 number of torsions (being respectively 29 times, 25 times, 32 times, 25 times), with Ni equivalent among the present invention's example No.1～No.19 that does not add crystal grain miniaturization element of table 1 21.7～22.1% and also tensile strength at 2000N/mm 2Or 2000N/mm 2Above No.3,11,12,18 number of torsions (being respectively 13 times, 13 times, 11 times, 13 times) are compared, and can find out the effect of adding crystal grain miniaturization element significantly.
But, in comparative example No.45, No.46, because of exceedingly having added Al or Nb, so number of torsions reduces on the contrary.
Below, the effect and seeking of narrating reduction hydrogen amount of the present invention reduces the effect of the manufacture method of hydrogen amount.Table 3 shows creating conditions of embodiment and characteristic.About the material that is for experiment, be with the steel grade A of table 1 hot carry out the rolling and solution treatment of wire rod down after, implement dehydrogenation under with the condition of a part in table 3 of this wire rod and handle.Implement then the intermediary hand-drawn wire until Φ 3.4mm, make crin, then, implement many continuous annealings (solution treatment) under the condition of each atmosphere gas in table 3, thereafter this crin is implemented the steel wire that precision work hand-drawn wire is processed into Φ 1.6mm.
The present invention example No.47～No.55 and comparative example No.56, No.57 are investigation crystal grain miniaturizations and add the example of crystal grain miniaturization element to the effect of the number of torsions of steel wire.
In the present invention's example No.47～No.55, because of the low number of torsions height of hydrogen amount.Particularly the present invention's example No.50～No.55 handles because of implementing dehydrogenation, has further reduced the hydrogen amount, so number of torsions also further improves.This has shown the effect by the high number of torsions that reduces the hydrogen generation.
In addition, comparative example No.56, No.57 anneal in containing the atmosphere of hydrogen, because of the hydrogen amount height in the material, so number of torsions is low.
Below, narrate the effect of hand-drawn wire working method of the present invention.Table 4 shows hand-drawn wire condition and the characteristic of embodiment, about the material that is for experiment, be with the steel grade I of the steel grade AH of table 2, table 1 and steel grade L with the hot rolling mode carry out wire rod rolling and implement solution treatment after, this wire rod is implemented the processing of intermediary hand-drawn wire until Φ 3.4mm, make crin, then, under argon gas atmosphere, implement many continuous annealings (solution treatment), with hand-drawn wire amount of finish in table 4 this crin implemented precision work hand-drawn wire processing, make steel wire thereafter.In addition, also show the scope of the hand-drawn wire amount of finish of the best of calculating by formula (3), formula (4) in the table 4.
The present invention example No.58～No.66 and comparative example No.67～No.72 are investigation hand-drawn wire amount of finish to the example of the effect of the tensile strength of steel wire, number of torsions, rigidity modulus.
The present invention's example No.58～No.66, because of the hand-drawn wire amount of finish is suitable, thus the tensile strength height, and show high number of torsions and rigidity modulus.
But, comparative example No.67, No.69, No.71, because of the hand-drawn wire amount of finish is low, so tensile strength is low, not only the effect of high number of torsions of the present invention is indeterminate, and strain to cause living martensite volume low, rigidity modulus is poor.
Comparative example No.68, No.70, No.72, the hand-drawn wire amount of finish is too high, and it is many to cause living martensite volume in response to change, and number of torsions is low.
As above embodiment shows, can know, high-strength stainless steel steel wire of the present invention is very good aspect number of torsions (prolonging toughness) and rigidity modulus.
Table 1
No. Steel grade Chemical ingredients (quality %) 2C+N (％) Ni equivalent (%) GI (％) Hydrogen amount (ppm) Average crystal grain diameter (μ m) Strain causes living horse for the scale of construction (volume %) Tensile strength (N/mm 2) Number of torsions (inferior) Rigidity modulus (GPa)
C Si Mn P S Ni Cr Mo Cu O N
Example of the present invention 1 A 0.1 0.8 1.6 0.03 0.0033 7 17 0.1 0.2 0.005 0.06 0.26 22.0 18.5 2.2 40 51 1990 17 67
2 B 0.04 0.8 1.5 0.02 0.0045 7 16.9 0.1 0.1 0.006 0.1 0.18 21.6 18.2 2 30 70 1910 14 68
3 C 0.13 0.8 1.5 0.04 0.0052 7 17.1 0.2 0.1 0.004 0.02 0.28 22.0 18.7 1.8 30 58 2050 13 69
4 D 0.03 0.8 1.5 0.03 0.0023 6.9 17 0.1 0.2 0.004 0.17 0.23 22.4 17.9 2.3 40 31 1850 40 66
5 E 0.1 0.2 1.6 0.03 0.0008 7 17.1 0.3 0.2 0.005 0.06 0.26 22.1 19.8 3 50 51 1990 32 66
6 F 0.1 2 1.5 0.02 0.0038 7 17 0.1 0.1 0.005 0.06 0.26 22.4 18.3 2.8 30 41 1950 35 66
7 G 0.1 3.5 1.5 0.03 0.0003 6.9 16.9 0.1 0.2 0.002 0.06 0.26 22.7 17.7 2.1 40 24 1880 40 65
8 H 0.08 0.8 0.3 0.03 0.0020 8.5 17 0.1 0.2 0.006 0.05 0.21 21.9 28.9 1.8 30 25 1790 43 63
9 I 0.1 0.7 3 0.02 0.0063 7 17 0.2 0.1 0.005 0.06 0.26 23.5 22.1 1.5 40 38 1940 36 65
10 J 0.11 0.8 4.5 0.03 0.0072 5.6 17 0.1 0.2 0.003 0.07 0.29 23.8 12.0 1.8 50 61 2080 12 69
11 K 0.1 0.8 0.5 0.03 0.0023 6.8 17.2 0.1 0.2 0.005 0.06 0.26 20.9 13.9 2.3 30 67 2050 13 70
12 L 0.11 0.8 1.6 0.04 0.0046 7.3 14.5 0.1 0.3 0.005 0.06 0.28 20.8 28.9 3.1 40 75 2120 11 67
13 M 0.09 0.8 1.3 0.03 0.0028 7.2 18.5 0.1 0.2 0.005 0.05 0.23 22.7 14.9 3.2 50 31 1850 25 65
14 N 0.09 0.8 1.4 0.04 0.0015 7.2 17 0.8 0.2 0.004 0.06 0.24 22.6 25.3 1.8 40 34 1880 38 65
15 O 0.08 0.8 1.3 0.03 0.0064 7 17.1 1.7 0.1 0.005 0.04 0.23 23.4 29.8 2.5 40 23 1820 46 64
16 P 0.07 0.8 1.3 0.03 0.0039 6.8 17.6 2.1 0.05 0.003 0.04 0.18 23.3 29.5 2.1 30 22 1820 40 63
17 Q 0.09 0.7 1.6 0.03 0.0088 7 17.1 0.1 0.2 0.003 0.06 0.24 22.0 18.0 2.7 50 56 1970 18 67
18 R 0.1 0.6 1.6 0.03 0.0012 6.9 17 0.1 0.2 0.009 0.05 0.25 21.8 17.5 2.2 40 63 2020 13 67
19 R 0.09 0.6 1.6 0.01 0.0007 7.1 17.1 0.1 0.2 0.009 0.06 0.24 22.0 18.9 2.2 40 54 1960 30 67
Comparative example 20 S 0.02* 0.8 1.6 0.03 0.003 7.2 17.1 0.1 0.2 0.005 0.06 0.1* 21.3 18.7 2.8 30 90* 1650 18 65
21 T 0.15* 0.6 1.6 0.03 0.003 6.9 17 0.1 0.1 0.005 0.04 0.34* 22.3 18.1 2.1 30 42 2100 2* 67
22 U 0.04 0.8 1.6 0.03 0.003 6.9 17 0.1 0.1 0.005 0.22* 0.3 23.2 19.0 1.9 40 0* 1850 3* 63
23 V 0.1 4.5* 1.4 0.03 0.003 6.8 16.8 0.1 0.2 0.005 0.05 0.25 22.7 16.8 2 40 25 1870 7* 65
24 W 0.08 0.8 6* 0.03 0.003 6.5 17.1 0.1 0.2 0.005 0.05 0.21 25.6 22.0 1.8 30 40 1850 8* 63
25 X 0.09 0.7 0.6 0.03 0.003 9.5* 17 0.1 0.2 0.005 0.05 0.23 23.3 38.7* 1.7 50 0* 1700 55 60*
26 Y 0.1 0.8 3.8 0.03 0.003 4.5* 17 0.1 0.2 0.005 0.05 0.25 21.6 0.3 2.2 40 95* 2280 1* 70
27 Z 0.09 0.7 1.5 0.03 0.003 7.2 13.8* 0.1 0.2 0.005 0.05 0.23 19.8* 29.4 2.3 30 95* 2180 2* 66
28 AA 0.09 0.8 1.4 0.03 0.003 7 19.6* 0.1 0.2 0.005 0.05 0.23 23.3 10.0 2.2 30 15* 1800 8* 62*
29 AB 0.08 0.7 1.3 0.03 0.003 6.8 16.8 3.5* 0.2 0.005 0.05 0.21 24.4* 43.4* 2.4 50 3* 1720 15 59*
30 AC 0.1 0.7 1.6 0.03 0.003 7.1 17 0.1 1.5* 0.005 0.06 0.26 22.1 19.4 2.5 40 1* 1660* 40 60*
31 AD 0.1 0.8 1.6 0.03 0.0082 6.9 17 0.1 0.2 0.014* 0.05 0.25 21.8 17.5 3.1 40 62 2010 5* 67
32 AE 0.09 0.6 1.6 0.03 0.015* 6.9 17 0.1 0.2 0.07 0.06 0.24 21.8 17.4 1.9 30 64 2000 7* 67
*: beyond the present invention.
Table 2
No. Steel grade Chemical ingredients (quality %) 2C+N (％) Ni equivalent (%) GI (％) Hydrogen amount (ppm) Average crystal grain diameter (μ m) Strain causes living horse for the scale of construction (volume %) Tensile strength (N/mm 2) Number of torsions (inferior) Rigidity modulus (GPa)
C Si Mn P S Ni Cr Mo Cu O N (other)
Example of the present invention 33 AF 0.1 0.7 1.7 0.03 0.0033 6.9 17 0.1 0.2 0.005 0.06 0.26 22.0 17.8 3.1 50 55.0 2000 18 67
34 AG 0.09 0.8 1.6 0.02 0.0043 7.1 16.9 0.2 0.1 0.002 0.05 Al；0.02 0.23 21.9 20.2 2.1 10 63.0 1980 34 67
35 AH 0.11 0.6 1.5 0.03 0.0008 7.1 17.1 0.3 0.1 0.004 0.04 Al；0.06 0.26 22.1 20.4 2.5 10 54.0 2000 29 68
36 AI 0.1 0.8 1.4 0.02 0.0029 7 17 0.1 0.2 0.002 0.06 Al；0.18 0.26 21.8 18.1 1.9 10 53.0 2000 25 68
37 AJ 0.1 0.8 1.4 0.02 0.0029 7 17 0.1 0.2 0.005 0.06 Nb；0.08 0.26 21.8 18.1 2.2 20 52.0 1990 31 67
38 AK 0.09 0.7 1.5 0.03 0.0035 6.9 17.1 0.2 0.1 0.006 0.05 Nb；0.25 0.23 21.7 17.6 3 10 70.0 2000 32 68
39 AL 0.1 0.8 1.6 0.03 0.0044 7 17 0.3 0.1 0.003 0.05 Ti；0.07 0.25 22.1 20.0 1.8 10 56.0 1980 24 67
40 AM 0.09 0.8 1.5 0.02 0.0008 7.2 17 0.2 0.1 0.003 0.05 Zr；0.22 0. 23 22.0 20.6 2.2 l0 58.0 1950 25 66
4l AN 0.09 0.8 1.5 0.02 0.0008 7.2 17 0.2 0.1 0.003 0.05 Ta；0.15 0.23 22.0 20.6 2.2 10 60.0 1950 23 67
42 AO 0.1 0.7 1.6 0.03 0.0016 7.1 16.9 0.1 0.2 0.004 0.06 W；0.17 0.26 22.0 19.7 2.2 20 50.0 1980 24 66
43 AP 0.09 0.8 1.5 0.02 0.0021 7 17 0.1 0.2 0.004 0.05 Al；0.03，Nb；0.1 0.23 21.7 18.0 2.2 10 54.0 1980 33 68
44 AO 0.1 0.7 1.5 0.02 0.0034 7.1 17.1 0.1 0.1 0.005 0.05 V；0.3 0.25 22.0 18.8 2.2 10 58.0 2010 25 87
Relatively 45 AR 0.09 0.7 1.6 0.03 0.0005 7.1 17.1 0.1 0.1 0.002 0.06 Al；0.38* 0.24 22.1 18.9 2.2 10 57.0 1970 5 57
46 AS 0.1 0.8 1.5 0.03 0.0011 7.1 17.1 0.1 0.1 0.005 0.06 Nb；0.50* 0.26 22.1 18.9 2.2 10 50.0 2000 6 66
*: beyond the present invention.
Table 3
No. Steel grade Dehydrogenation is handled The gas of many continuous annealing atmosphere Hydrogen amount (ppm) Average crystal grain diameter (μ m) Strain causes living martensite volume (volume %) Tensile strength (N/mm 2) Number of torsions (inferior) Rigidity modulus (GPa)
Example of the present invention 47 A Be untreated Argon gas 2.2 10 60 2000 17 67
48 A Be untreated Nitrogen 2.5 10 63 1980 17 67
49 A Be untreated Atmosphere 2.1 10 61 2050 16 68
50 A 300 ℃-24h, atmosphere Argon gas 0.8 10 58 2040 22 67
51 A 300 ℃-24h, nitrogen Argon gas 0.9 10 62 2030 21 68
52 A 250 ℃-24h, atmosphere Argon gas 1.2 10 63 2000 20 67
53 A 150 ℃-24h, atmosphere Argon gas 2 10 65 1990 18 67
54 A 450 ℃-24h, atmosphere Argon gas 0.7 10 59 2020 25 68
55 A 550 ℃-24h, atmosphere Argon gas 1.1 10 60 2030 22 68
Relatively 56 A Be untreated Hydrogen-containing gas * 6.3* 10 61 2050 7* 66
57 A 300 ℃-24h, atmosphere Hydrogen-containing gas * 5.3* 10 62 2100 5* 65
*: beyond the present invention.
Table 4
No. Steel grade Ni equivalent (%) The hand-drawn wire amount of finish, the ε optimum range Actual hand-drawn wire amount of finish; ε Hydrogen amount (ppm) Average crystal grain diameter (μ m) Strain causes living martensite volume (volume %) Tensile strength (N/mm 2) Number of torsions (inferior) Rigidity modulus (GPa)
Example of the present invention 58 AH 22.1 1.035～2.435 1.51 2.4 10 55 2000 29 68
59 AH 22.1 1.035～2.435 1.1 6 2.3 10 30 1860 43 65
60 AH 22.1 1.035～2.435 2.08 2.1 10 75 2210 12 68
61 I 23.5 1.245～2.645 1.51 1.8 40 40 1950 34 65
62 I 23.5 1.245～2.645 1.27 2 40 25 1820 48 64
63 I 23.5 1.245～2.645 2.45 2.1 40 76 2080 20 66
64 L 20.8 0.84～2.24 1.51 2.8 30 70 2100 12 67
65 L 20.8 0.84～2.24 0.87 2.5 30 30 1830 19 64
66 L 20.8 0.84～2.24 2.00 2.4 30 78 2200 10 68
Comparative example 67 AH 22.1 1.035～2.435 0.96* 2.5 10 18* 1650 45 62*
68 AH 22.1 1.035～2.435 2.45* 2.3 10 83* 2200 5* 68
69 I 23.5 1.245～2.645 1.06* 1.9 40 10* 1640 50 62*
70 I 23.5 1.245～2.645 2.89* 2.3 40 84* 2240 5* 66
71 L 20.8 0.84～2.24 0.78* 2.8 30 18* 1680 23 62*
72 L 20.8 0.84～2.24 2.45* 3 30 90* 2240 2* 68
*: outside the scope of the invention.
According to toughness rigidity modulus good high-strength stainless steel steel wire and the manufacture method thereof of prolonging of the present invention, except the basal component and purity (oxygen, sulphur) of the parent metal of regulation austenite stainless steel steel wire, limit tissue, intensity and hand-drawn wire processing conditions, use crystal grain miniaturization and the heat treated highly malleablized effect of ausforming, the high-strength stainless steel steel wire that can stably be significantly improved and prolong toughness and rigidity modulus.

Claims (4)

1. high-strength stainless steel steel wire that the number of torsions rigidity modulus is good, it is characterized in that, in quality %, contain C:0.03～0.14%, Si:0.1～4.0%, Mn:0.1～5.0%, Ni:5.0～9.0%, Cr:14.0～19.0%, N:0.005～0.20%, O:0.001～0.01%, S:0.0001～0.012%, and then contain following (i), (ii) wantonly more than a kind or a kind, and contain as required (iii), all the other are made of Fe and unavoidable impurities, and, 2C+N is 0.17～0.32%, the value of the Ni equivalent % of following formula (1) is 20～24, H≤4ppm, the value of the GI% of following formula (2) is below 30 or 30
(i): Al, Nb, Ti, Zr, Ta, W's is wantonly more than a kind or a kind, is respectively 0.01～0.30%;
(ii): V is 0.1～0.5%;
(iii): Mo is 0.2～3.0%;
Ni equivalent %=Ni+0.65Cr+0.98Mo+1.06Mn+0.35Si+12.6 (C+N) (1)
GI％＝16C+2Mn+9Ni-3Cr+8Mo+15N (2)。
2. the manufacture method of the good high-strength stainless steel steel wire of a number of torsions rigidity modulus, it is characterized in that, will be in quality %, contain C:0.03～0.14%, Si:0.1～4.0%, Mn:0.1～5.0%, Ni:5.0～9.0%, Cr:14.0～19.0%, N:0.005～0.20%, O:0.001～0.01%, S:0.0001～0.012%, and then contain following (i), (ii) wantonly more than a kind or a kind, and contain as required (iii), all the other are made of Fe and unavoidable impurities, and, 2C+N is 0.17～0.32%, the value of the Ni equivalent % of following formula (1) is 20～24, the value of the GI% of following formula (2) is after the steel below 30 or 30 carries out hot rolling and makes wire rod and carry out solution treatment, this wire rod is carried out after solution treatment more than 1 time or 1 time and hand-drawn wire be processed into crin, implementing the precision work hand-drawn wire is processed in the series of processes of steel wire, at least last solution treatment is carried out in the atmosphere of hydrogen not, making H in the steel is 4ppm or below the 4ppm, according to carrying out the processing of precision work hand-drawn wire with the mode of cold drawn wire amount of finish ε in the scope of formula (4) of formula (3) expression
(i): Al, Nb, Ti, Zr, Ta, W's is wantonly more than a kind or a kind, is respectively 0.01～0.30%;
(ii): V is 0.1～0.5%;
(iii): Mo is 0.2～3.0%;
Ni equivalent %=Ni+0.65Cr+0.98Mo+1.06Mn+0.35Si+12.6 (C+N) (1)
GI％＝16C+2Mn+9Ni-3Cr+8Mo+15N (2)
ε＝ln(A 0/A) (3)
Wherein, A 0: the wire rod before the hand-drawn wire processing or the basal area of crin
A: the basal area of the steel wire after the hand-drawn wire processing
0.15 * (Ni equivalent)-2.28≤ε≤0.15 * (Ni equivalent)-0.88 (4).
3. the manufacture method of the high-strength stainless steel steel wire that number of torsions rigidity modulus as claimed in claim 2 is good, it is characterized in that, in aforementioned series of processes, additional operation prior to the solution treatment in the atmosphere of hydrogen not, carried out, in this additional process, in 200 ℃～600 ℃ atmosphere of hydrogen not, implement dehydrogenation and handle.
4. according to the manufacture method of the good high-strength stainless steel steel wire of claim 2 or 3 described number of torsions rigidity modulus, it is characterized in that the austenite average crystal grain diameter before the hand-drawn wire processing of above-mentioned wire rod or crin is 30 μ m or below the 30 μ m.
CNB02813737XA 2002-05-08 2002-05-08 High strength stainless steel wire excellent in ductility-toughness and modulus of rigidity and method for production thereof Expired - Lifetime CN1263880C (en)

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JPWO2003095693A1 (en) 2005-09-15
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