CN105579595A - High tensile strength steel wire - Google Patents
High tensile strength steel wire Download PDFInfo
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- CN105579595A CN105579595A CN201480052870.1A CN201480052870A CN105579595A CN 105579595 A CN105579595 A CN 105579595A CN 201480052870 A CN201480052870 A CN 201480052870A CN 105579595 A CN105579595 A CN 105579595A
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/02—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for springs
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
- B21C1/00—Manufacture of metal sheets, metal wire, metal rods, metal tubes by drawing
- B21C1/003—Drawing materials of special alloys so far as the composition of the alloy requires or permits special drawing methods or sequences
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
- C21D1/25—Hardening, combined with annealing between 300 degrees Celsius and 600 degrees Celsius, i.e. heat refining ("Vergüten")
-
- 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
-
- 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
-
- 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
-
- 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
-
- 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
- C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
-
- 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
Abstract
A high tensile strength steel wire having as steel composition: a carbon content ranging from 0.20 weight percent to 1.00 weight percent, e.g. from 0.3 weight percent to 0.85 weight percent, e.g. from 0.4 weight percent to 0.7 weight percent, e.g. from 0.5 weight percent to 0.6 weight percent, a silicon content ranging from 0.05 weight percent to 2.0 weight percent, e.g. from 0.2 weight percent to 1.8 weight percent, e.g. from 1.2 weight percent to 1.6 weight percent, a manganese content ranging from 0.40 weight percent to 1.0 weight percent, e.g. from 0.5 weight percent to 0.9 weight percent, a chromium content ranging from 0.0 weight percent to 1.0 weight percent, e.g. from 0.5 weight percent to 0.8 weight percent, a sulfur and phosphor content being individually limited to 0.05 weight percent, e.g. limited to 0.025 weight percent, contents of nickel, vanadium, aluminum, copper or other micro-alloying elements all being individually limited to 0.5 weight percent, e.g. limited to 0.2 weight percent, e.g. limited to 0.08 weight percent, the remainder being iron, said steel wire having martensitic structure, wherein at least 10 volume percent of martensite are oriented.
Description
Technical field
The present invention relates to a kind of high-tensile steel wires, a kind of method for the manufacture of high-tensile steel wires and such high-tensile steel wires are as spring wire or for the production of the purposes of the element of rope or application.
Background technology
Spring is made up of Steel Alloy usually.The most frequently used spring steel is piano wire, oil temper wire, chrome-silicon, chrome alum and 302 and 17-7 stainless steel.By more high quality, more high strength modification that the spring wire of chrome-silicon, chrome alum manufacture is oil temper wire.
The spring steel be used in the application of such as automobile valve spring is generally required to have very high tensile strength and bending strength.Tensile strength is that material repels is attempted to pull open or stretch its ability.Tensile strength is key property to the silk applied for spring.Such as, the extension spring higher than its tensile strength work will rupture.
In general, when production small size, high-strength spring, for the drawn steel wire of high-strength spring purposes by Quench and temper to give the higher strength of materials in drawn steel wire, then by cold coiling to obtain coil spring shape.For this reason, require that be first used for high-strength spring application is not only had high strength by the steel wire that then drawing is heat-treated, but also have sufficiently high workability, it can not rupture when cold coiling.
Spring, the spring being particularly used to motor car engine, clutch coupling etc. is required to provide advanced performance, to deal with the trend towards more light weight and the more automobile of advanced feature.For this reason, the steel wire with more high strength and more high-durability is desired by spring.That adjustment is for the composition of the steel of spring wire for improving the main trend of character.In US2012/0291927A1, disclose an example, wherein, in steel wire, the content of C, Si, Mn and Cr is suggested to strict control, and Cr and Si therebetween in steel wire is set at suitable amount.But have found that, consider the preliminary shaping and bending operation that must carry out about spring wire, increase physical strength exceeds certain limit and this steel will be caused to have not enough ductility.Carry out a large amount of effort to improve steel wire to have higher tensile strength, there is acceptable ductility simultaneously.
Summary of the invention
An object of the present invention is to provide a kind of high-tensile steel wires with acceptable ductility.
Another object of the present invention is to provide a kind of high-tensile steel wires being suitable as spring wire.
Another object of the present invention is to provide suitable method to manufacture the high-tensile steel wires with acceptable ductility.
The invention describes because unidirectional martensite microtexture has the steel wire of very high strength and ductility, and in successive processes, produce the method for such steel wire.
According to a first aspect of the invention, a kind of high-tensile steel wires with following steel composition is provided:
Carbon content, scope is from 0.20% weight percent to 1.00% weight percent, such as, from 0.3% weight percent to 0.85% weight percent, such as, from 0.4% weight percent to 0.7% weight percent, such as from 0.5% weight percent to 0.6% weight percent
Silicone content, scope is from 0.05% weight percent to 2.0% weight percent, such as, from 0.2% weight percent to 1.8% weight percent, such as, from 1.2% weight percent to 1.6% weight percent,
Fe content, scope is from 0.40% weight percent to 1.0% weight percent, such as, from 0.5% weight percent to 0.9% weight percent,
Chromium content, scope is from 0.0% weight percent to 1.0% weight percent, such as, from 0.5% weight percent to 0.8% weight percent,
Sulphur and phosphorus content, be restricted to 0.05% weight percent respectively, such as, be restricted to 0.025% weight percent,
The content of nickel, vanadium, aluminium, copper or other microalloy element, is all restricted to 0.5% weight percent respectively, such as, is restricted to 0.2% weight percent, such as, be restricted to 0.08% weight percent
Remaining is iron,
Described steel wire has martensitic structure,
Wherein martensitic at least 10% volume percent is directed.
Preferably, martensitic at least 20% volume percent is directed.More preferably, martensitic at least 30% volume percent is directed.Most preferably, martensitic at least 40% volume percent is directed.
It is known that martensitic steel is a kind of polycrystalline material.When the crystal grain of polycrystalline material is by random orientation, polycrystalline material is not directed or without texture.Under given conditions, the crystal grain of polycrystalline material can by preferably directed, and in this case, and polycrystalline material is called as by " directed " or " veining ".Usually in the face of the orientation of two types, i.e. " crystal orientation " and " microtexture is directed ".Crystal orientation refers to that crystal grain is by crystal orientation, such as has preferred arrangement or the orientation in some crystal face or crystal orientation.Preferred crystal orientation is normally determined from the orientation dependency analysis of diffraction peak intensity (such as being analyzed or electronics backscattering diffraction (EBSD) by X-ray diffraction (XRD)), and it is measured on different direction in spaces in the system of coordinates of sample.On the other hand, if the crystal grain of polycrystalline material has anisotropic form shapes, during polycrystalline is formed, crystal grain also can be had by such as uniaxial compression " microtexture is directed "." microtexture is directed " means that the crystal grain of Anisotropic shapes is directed by morphology in preferred orientations or plane.This is by image analysis, and such as scanning electronic microscope (SEM) detects.In addition, crystal orientation is usually relevant with microtexture orientation, because the shape anisotropy of crystal grain is usually relevant to their crystallography.
Martensite occurs as strip or plate-like grain.When seeing at cross section, lensing (lens shaped) crystal grain is described to needle-like (aciculiform) sometimes.According to the application, in produced martensitic steel wire, at least 10% volume percent in martensite is directed.Term " directed " refer to lenticular grain by crystal orientation or microtexture directed, or crystallization and microtexture all directed.
The % volume percent of crystalline arrangement or orientation can be passed through X-ray diffraction (XRD) and analyze or electronics backscattering diffraction (EBSD) acquisition.The % volume percent of microtexture arrangement or orientation can be assessed by image analysis.
In this article, term " directed " not only meaning in the axis of crystallographic axis or lenticular grain and Fig. 1 by a
1and a
2shown equidirectional by accurate orientation, and refers to the orientation in tolerance zone.When the direction of some axle of crystal grain (or some crystallization direction) is as represented by angle [alpha] in FIG, in 20 °, preferably in 10 °, when more preferably departing from 5 °, these crystal grain are also considered to directed.
Arrangement or orientation at least refer to such as in the direction perpendicular to lenticular grain plane (as a in by Fig. 1
1, a
2shown direction, such as [001]) on, one dimension preferred orientation.Directed for one dimension, the direction of lenticular grain in lensing plane is (as a in FIG
4, a
5shown direction) upper stochastic distribution.
Preferably, according to the application, steel wire has bending strength Rp0.2, and it is at least 80% of tensile strength Rm.Rp0.2 is the bending strength under 0.2% tensile-permanent set.More preferably, bend Lapie, namely Rp0.2/Rm is between 80% to 95%.Therefore, the steel wire after recoverable deformation still can be deformed to a certain degree before breaking.
Steel wire according to the application preferably has corrosion-resistant finishes.More preferably, this steel wire has the corrosion-resistant finishes of any one be selected from zinc, nickel, silver, copper or their alloy.In this case, even if under the corrosive environment of harshness, steel wire also has the life-span of prolongation.
Steel wire according to the application can be in cold drawing state and have circular cross section.Steel wire can have the tensile strength Rm of at least 2000MPa for the steel wire diameter higher than 5.0mm, for the tensile strength of at least 2100MPa of the steel wire diameter higher than 3.0mm, the tensile strength at least 2200MPa of the steel wire diameter higher than 0.5mm is used for the steel wire that diameter is greater than 0.5mm.Preferably, long-pendingly after the fracture that this steel wire has at least 45% to reduce, and long-pendingly after the fracture more preferably with at least 50% to reduce.
In this article, the ductility of steel wire is obtained by tension test.The ductility of steel wire reduces instruction by post-rift area." area minimizing " is the difference after the original cross-sectional sum test of sample between its smallest cross-section area.The per-cent that it is represented as original cross-sectional usually reduces.Minimum cross-section is measured after steel wire fracture.
Wire drawing is used to by means of single or a series of die drawing silk to reduce the method for metal working of the cross section of silk.It is known that wire drawing improves the tensile strength Rm of steel wire and reduces ductility simultaneously.But compared with traditional cold drawing steel wire, the steel wire of the present invention with specific composition has suitable ductility and high tensile strength.
According to a second aspect of the invention, steel wire can be used as spring wire or the element for the production of rope.
According to a third aspect of the invention we, provide a kind of method that manufacture has high-tensile steel wires, described steel wire has as steel composition:
Carbon content, scope is from 0.20% weight percent to 1.00% weight percent, such as, from 0.3% weight percent to 0.85% weight percent, such as, from 0.4% weight percent to 0.7% weight percent, such as from 0.5% weight percent to 0.6% weight percent
Silicone content, scope is from 0.05% weight percent to 2.0% weight percent, such as, from 0.2% weight percent to 1.8% weight percent, such as, from 1.2% weight percent to 1.6% weight percent,
Fe content, scope is from 0.40% weight percent to 1.0% weight percent, such as, from 0.5% weight percent to 0.9% weight percent,
Chromium content, scope is from 0.0% weight percent to 1.0% weight percent, such as, from 0.5% weight percent to 0.8% weight percent,
Sulphur and phosphorus content, be restricted to 0.05% weight percent respectively, such as, be restricted to 0.025% weight percent,
The content of nickel, vanadium, aluminium, copper or other microalloy element is all restricted to 0.5% weight percent respectively, such as, be restricted to 0.2% weight percent, such as, be restricted to 0.08% weight percent,
Remaining is iron,
Described steel wire has martensitic structure,
Wherein martensitic at least 10% volume percent is directed.
Described method comprises the step of following order:
A) more than steel wire rod or steel wire austenitizing to Ac3 temperature is made in during being less than the cycle of 120 seconds,
B) during being less than the cycle of 60 seconds, make described austenitizing steel wire rod or quenching steel wire to lower than 100 DEG C,
C) be the steel wire rod that quenches described in the chien shih of 320 DEG C and 500 DEG C during cycle of 10 seconds to 600 seconds or steel wire tempering in scope,
D) quench and the steel wire rod of tempering or steel wire described in work hardening.
In the prior art, such as United States Patent (USP) 5922149A open in, steel wire/wire rod be first deformed or work hardening to final size, thereafter by Quench and temper, as shown schematically in fig. 2.On the contrary, in the present invention, first steel wire is quenched to form martensitic microstructure.Tempering following closely.The martensitic steel wire of tempering is then such as deformed by wire drawing or work hardening becomes final size, as being schematically shown in figure 3.
The present invention obtains beyond thought technological achievement and advantage.In usual online treatment, Quench and temper is final step, and martensite is claimed to wire drawing it is harmful always.Very high according to the tensile strength of martensite silk of the present invention, and the combination of tensile strength level and high-level ductility is rare.Because steel is relative to the specific alloy (having Cr and Si microalloying) of traditional eutectoid steel by carrying out the surprising the possibility of result of wire drawing acquisition to the martensite of tempering.The synergistic effect of the method for this composition and the application produces the martensitic steel wire with preferred martensite orientation.In cold drawing steel wire, martensite orientation is the result being applied force of compression by wire drawing in the martensitic steel wire of Quench and temper.
The method also can comprise step e) make the steel wire of described work hardening aging at temperature between 100 DEG C and 250 DEG C.
Preferably, described work hardening occurs in the temperature lower than 400 DEG C in this method.More preferably, described work hardening is cold drawing.Cold drawing has the bonus effect of work hardening and reinforcement material, thus further increases the mechanical characteristics of material.It also improves surface smoothness and keeps tighter tolerance, thus allows the quality of the expectation do not obtained by thermal distortion.Alternately, described work hardening is between 200 DEG C and 700 DEG C, and the temperature such as occurred between 200 DEG C to 400 DEG C is pulled out.For similar minimizing, the application that temperature is pulled out significantly reduces passage and simplifies technique.
Accompanying drawing explanation
When considering in conjunction with limiting examples and accompanying drawing, with reference to describing in detail, the present invention will be better understood, wherein:
Fig. 1 diagrammatically illustrates the crystal grain arrangement or directed in many crystalline materials.
Fig. 2 shows according to the thermal-mechanical treatment of prior art for steel wire.
Fig. 3 shows according to the thermal-mechanical treatment of the present invention for steel wire.
Fig. 4 shows for heat treated temperature according to the present invention time curve.
Fig. 5 compares the work hardening curve of prior art patent steel wire and the steel wire of the present invention according to the first embodiment of the present invention.
Fig. 6 compares the tensile strength of the function reduced as cross section of three passage drawing processs and six passage drawing processs.
Fig. 7 (a) shows the scanning electron microscopy structure (SEM) according to the vertical section of steel wire of the present invention, and Fig. 7 (b) shows the scanning electron microscopy structure of the vertical section with reference to steel wire with identical ratio of enlargement.
Fig. 8 (a) shows the scanning electron microscopy structure (SEM) according to the vertical section of steel wire of the present invention with lower ratio of enlargement, and Fig. 8 (b) shows the scanning electron microscopy structure (SEM) of the vertical section with reference to steel wire with identical ratio of enlargement.
Embodiment
Fig. 4 shows and is applied to suitable temperature on steel wire or wire rod to time curve, and this steel wire or gauge or diameter of wire are 5.29mm and have following steel composition:
-C% weight percent=0.55
-Si% weight percent=1.4
-Cr% weight percent=0.6
-Mn% weight percent=0.7
All the other are iron and inevitable impurity.
The starting temperature M of the martensitic transformation of this steel
sfor about 280 DEG C, and martensite forms the temperature M terminated
ffor about 100 DEG C.
Each step of the method is as follows:
-the first austenitizing step (10), during this period, steel wire rested in the stove of about 950 DEG C during 120 seconds,
-the second quenching Step (12), for carrying out martensitic transformation in oil during at least 20 seconds at lower than the temperature of 100 DEG C,
-three tempering step (14), for increasing toughness during being less than 60 seconds at higher than the temperature of 320 DEG C; With
-during 20 seconds or longer time the 4th cooling step (16) at room temperature.
Curve 18 is the temperature curves in each equipment unit (stove, bath ...), and curve 19 is temperature of steel wire.
After above-mentioned thermal treatment, steel wire or wire rod mainly have martensitic microstructure.Because martensite is to H-embrittlement-sensitive, heat treated steel wire is pickling-free by direct cold drawing, and oil can be used as lubricant, for drawing process subsequently.
The martensitic steel wire formed or wire rod proceed a series of drawing process, such as the drawing process of six passages.
For this six passages technique steel wire every time after diameter, diameter reduce, cross section reduce, accumulation cross section reductions, tensile strength, tensile strength change and area minimizing summarize all in Table 1.In this article, " diameter reduction " and " cross section reduction " refer to the minimizing after each passage of wire drawing." diameter reduction " should mean that gauge of wire was poor before and after each passage, and the per-cent diameter be represented as with respect to its green diameter before wire-drawing die reduces.Similarly, " cross section reduction " means the difference of the cross-sectional area of steel wire before and after each passage, and the per-cent cross section be represented as with respect to its original section before wire-drawing die reduces.
As shown in table 1, about 5% is reduced to for every time diameter.By means of more multi-pass, the tensile strength of steel wire increases further.After by six passage wire drawings, steel wire has diameter and the 2151N/mm of 3.86mm
2tensile strength.More than six passages, the bending strength Rp0.2 of steel wire is at least 80% of tensile strength Rm.In addition, steel wire entirety has enough ductility, and it is depicted as more than 46.5% by area minimizing and the breaking part breaking elongation of wire drawing is more than 2%.
Fig. 5 is shown according to the work hardening curve (Q & TCrSi) of cold drawn wire drawing of the present invention with compared with silk (R-SW).Contain the carbon of 0.8% weight percent with reference to silk and quenched in lead.There is with reference to silk initial diameter and the 1360N/mm of 6.5mm
2tensile strength.By replacing by Quench and temper operating with reference to the patenting of silk, the martensite of meticulous tempering can be obtained, its tensile strength at least 400N/mm higher than the silk of patenting
2.The work hardening curve of the martensite silk (Q & TCrSi) of cold drawing tempering has the slope similar with patenting silk (R-SW).This means to reduce for same or analogous cross section, these two steel wires demonstrate comparable intensity to be increased.For identical cross section reduction, steel wire of the present invention is by least 400N/mm stronger than the silk of drawing after patenting
2.
This very high tensile strength of silk of the present invention can owing to the formation of the martensitic microstructure after distortion or work hardening in steel wire, and the martensitic crystal grains of particularly directed certain percentage, it can be observed in image analysis.
Table 1: there is the initial diameter of 5.29mm, with six passages by the characteristic of wire drawing to the steel wire of 3.86mm diameter.
embodiment 2
In the present embodiment, the thermal treatment being similar to embodiment 1 is applied to steel wire, and its diameter is 3.75mm, and has following steel composition:
-C% weight percent=0.55
-Si% weight percent=1.4
-Cr% weight percent=0.6
-Mn% weight percent=0.7
All the other are iron and inevitable impurity.
After thermal treatment, steel wire mainly has martensitic microstructure.Steel wire stands six passage drawing step further, and its diameter is reduced to 2.8mm.After each passage, the characteristic of steel wire is shown in Table 2.Although obtain high tensile strength after six passages, steel wire still has as reduced by the area of 52.8% the enough ductility represented.And the ductility of steel wire is guaranteed during whole drawing process, this can be reduced by the area of steel wire after one to six passage all verifies more than 52.8%, as shown in table 2.
Table 2: there is the initial diameter of 3.75mm, with six passages by the characteristic of wire drawing to the steel wire of 2.88mm diameter
embodiment 3
In this example, be with the difference of the sample of embodiment 2, after similar thermal treatment, the martensitic steel wire with 3.75mm diameter by three passages by wire drawing.
Reduced by the diameter after each passage of this three passages technique steel wire, diameter, cross section reduces, accumulation cross section reductions, tensile strength, tensile strength change and area minimizing summarize in table 3.
For three passage techniques, every time mean diameter is reduced to about 9.5%, and it is the almost twice of six passage techniques as shown in embodiment 1 and 2.The function that the tensile strength (Rm) of three passage wire drawings (SW3) reduces (Δ S) as cross section is drawn in figure 6, and the tensile strength of six passage wire drawings of itself and embodiment 1 (SW1) and embodiment 2 (SW2) is formed and contrasts.As shown in Figure 6, the increase almost reduced with cross section for the increase of three and six passes of drawing steel wire tensile strength is proportional.As compared to the silk of experience six passage technique (SW1 with SW2), as shown in Figure 6, the slope experiencing the tensile strength trend curve of three passage technique (SW3) silks is slightly large, and namely reduce for similar cross section, tensile strength increases even higher.The silk experiencing three passages reduces demonstrate 8N/mm for the cross section of 1%
2average intensity increase, and the silk experiencing six passages for 1% cross section reduce and demonstrate 6N/mm
2average intensity increase.In addition, by the steel wire of three passes of drawing, there is even better ductility.After one to three passage, the area of steel wire reduces all more than 53.6%.After three passages, drawn steel wire has excellent characteristic: tensile strength is 2300N/mm
2, and area is reduced to 53.6%, and it exceedes the standard-required for Quench and temper spring wire.
Table 3: there is the initial diameter of 3.75mm, with three passages by the characteristic of wire drawing to the steel wire of 2.8mm diameter.
This very high tensile strength can be the result of the martensitic crystal grains of the orientation of steel wire after wire drawing.Studied according to the microtexture of drawn steel wire of the present invention.Adopt by the steel wire of conventional process as a reference, namely as shown in Figure 2, first by wire drawing, then by Quench and temper.Steel wire of the present invention and reduce with reference to the composition of steel wire, cross section and thermal treatment closely similar.
Experience the microtexture of the vertical section of the steel wire of three passages according to the present invention shown in Fig. 7 (a), and the microtexture of the vertical section of reference steel wire is shown in Fig. 7 (b).Vertical section is the cross section at longitudinal direction or length direction at steel wire.As shown in Fig. 7 (b), show uniform martensitic microstructure with reference to steel wire.Martensitic crystal grains is in whole region random orientation.In contrast, for steel wire of the present invention, show martensitic microstructure and martensitic crystal grains preferably orientation as Suo Shi Fig. 7 (a).In this longitudinal cross-section view, martensitic crystal grains occurs needle-like (aciculiform) and the longer axis parallel of needle-like aligns in wire-drawing direction (being parallel to the scale direction in Fig. 7).This shows, the normal direction of lensing (lens shaped) crystal grain is preferably perpendicular to wire-drawing direction orientation.
Fig. 8 (a) and (b) are the vertical section of the steel wire of the present invention under lower ratio of enlargement and the microtexture with reference to steel wire respectively.It confirms that the martensitic microstructure (Fig. 8 (a)) of the orientation according to steel wire of the present invention is to the stochastic distribution martensitic microstructure (Fig. 8 (b)) with reference to steel wire.
By image analysis, the steel wire according to an experience of the present invention passage demonstrates the unidirectional martensite being at least 10% volume percent, and the steel wire that experienced by three passages demonstrates the unidirectional martensite being at least 20% volume percent.
Claims (15)
1. a high-tensile steel wires, it has following steel composition:
Carbon content, scope is from 0.20% weight percent to 1.00% weight percent, such as, from 0.3% weight percent to 0.85% weight percent, such as, from 0.4% weight percent to 0.7% weight percent, such as from 0.5% weight percent to 0.6% weight percent
Silicone content, scope is from 0.05% weight percent to 2.0% weight percent, such as, from 0.2% weight percent to 1.8% weight percent, such as, from 1.2% weight percent to 1.6% weight percent,
Fe content, scope is from 0.40% weight percent to 1.0% weight percent, such as, from 0.5% weight percent to 0.9% weight percent,
Chromium content, scope is from 0.0% weight percent to 1.0% weight percent, such as, from 0.5% weight percent to 0.8% weight percent,
Sulphur and phosphorus content are restricted to 0.05% weight percent respectively, such as, be restricted to 0.025% weight percent,
The content of nickel, vanadium, aluminium, copper or other microalloy element is all restricted to 0.5% weight percent respectively, such as, be restricted to 0.2% weight percent, such as, be restricted to 0.08% weight percent
Remaining is iron,
Described steel wire has martensitic structure,
Wherein martensitic at least 10% volume percent is directed.
2. high-tensile steel wires according to claim 1, wherein martensitic at least 20% volume percent is directed.
3. high-tensile steel wires according to claim 1, wherein martensitic at least 40% volume percent is directed.
4. the high-tensile steel wires according to any one in aforementioned claim, wherein said steel wire has the bending strength of Rp0.2, and it is at least 80% of described tensile strength Rm.
5. the high-tensile steel wire according to any one in aforementioned claim, wherein said steel wire has corrosion-resistant coating.
6. high-tensile steel wires according to claim 5, wherein said corrosion-resistant coating is selected from any one in zinc, nickel, silver, copper or their alloy.
7. the high-tensile steel wires according to any one in aforementioned claim, described steel wire is in cold drawing state and has circular cross section.
8. the high-tensile steel wires according to any one in aforementioned claim, wherein said steel wire has the tensile strength Rm of at least 2000MPa for the steel wire diameter higher than 5.0mm, for the tensile strength of at least 2100MPa of the steel wire diameter higher than 3.0mm, for the tensile strength of at least 2200MPa of the steel wire diameter higher than 0.5mm.
9. the high-tensile steel wires according to any one in aforementioned claim, wherein said steel wire has the post-rift area minimizing of at least 45%.
10. the high-tensile steel wires according to any one in aforementioned claim, wherein said steel wire has the post-rift area minimizing of at least 50%.
11. high-tensile steel wires according to any one in aforementioned claim are as the purposes of spring wire or the element for the production of rope.
12. 1 kinds of methods manufacturing high-tensile steel wires, described steel wire has following steel composition:
Carbon content, scope is from 0.20% weight percent to 1.00% weight percent, such as, from 0.3% weight percent to 0.85% weight percent, such as, from 0.4% weight percent to 0.7% weight percent, such as from 0.5% weight percent to 0.6% weight percent
Silicone content, scope is from 0.05% weight percent to 2.0% weight percent, such as, from 0.2% weight percent to 1.8% weight percent, such as, from 1.2% weight percent to 1.6% weight percent,
Fe content, scope is from 0.40% weight percent to 1.0% weight percent, such as, from 0.5% weight percent to 0.9% weight percent,
Chromium content, scope is from 0.0% weight percent to 1.0% weight percent, such as, from 0.5% weight percent to 0.8% weight percent,
Sulphur and phosphorus content are restricted to 0.05% weight percent respectively, such as, be restricted to 0.025% weight percent,
The content of nickel, vanadium, aluminium, copper or other microalloy element is all restricted to 0.5% weight percent respectively, such as, be restricted to 0.2% weight percent, such as, be restricted to 0.08% weight percent
Remaining is iron,
Described steel wire has martensitic structure,
Wherein martensitic at least 10% volume percent is directed;
Described method comprises following sequenced step:
A) during being less than the cycle of 120 seconds, make more than steel wire rod or steel wire austenitizing to Ac3 temperature,
B) during being less than the cycle of 60 seconds, make the steel wire rod of described austenitizing or quenching steel wire to lower than 100 DEG C,
C) be the steel wire rod that quenches described in the chien shih of 320 DEG C and 500 DEG C during cycle of 10 seconds to 600 seconds or steel wire tempering in scope,
D) quenching described in work hardening the steel wire rod of tempering or steel wire.
The method of 13. manufacture high-tensile steel wires according to claim 12, wherein said method then following steps further:
E) make the steel wire of described work hardening aging at the temperature between 100 DEG C and 250 DEG C.
The method of 14. manufacture high-tensile steel wires according to claim 12 or 13, wherein said work hardening occurs at lower than the temperature of 700 DEG C.
15. according to claim 12 to the method for the manufacture high-tensile steel wires described in any one in 14, and wherein said work hardening is cold drawing.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| EP13188231.8 | 2013-10-11 | ||
| EP13188231 | 2013-10-11 | ||
| PCT/EP2014/070843 WO2015052035A1 (en) | 2013-10-11 | 2014-09-30 | High tensile strength steel wire |
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|---|---|
| CN105579595A true CN105579595A (en) | 2016-05-11 |
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| CN201480052870.1A Pending CN105579595A (en) | 2013-10-11 | 2014-09-30 | High tensile strength steel wire |
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| Country | Link |
|---|---|
| US (1) | US20160237518A1 (en) |
| EP (1) | EP3055436B1 (en) |
| KR (1) | KR20160068765A (en) |
| CN (1) | CN105579595A (en) |
| AU (1) | AU2014334010A1 (en) |
| BR (1) | BR112016007217A2 (en) |
| DK (1) | DK3055436T3 (en) |
| ES (1) | ES2640626T3 (en) |
| HR (1) | HRP20171447T1 (en) |
| HU (1) | HUE034437T2 (en) |
| MY (1) | MY176216A (en) |
| PL (1) | PL3055436T3 (en) |
| PT (1) | PT3055436T (en) |
| RS (1) | RS56504B1 (en) |
| SI (1) | SI3055436T1 (en) |
| WO (1) | WO2015052035A1 (en) |
| ZA (1) | ZA201601568B (en) |
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| CN106399826A (en) * | 2016-08-30 | 2017-02-15 | 湖北立晋钢铁集团有限公司 | Spring flat steel for automobile and manufacturing method of spring flat steel |
| CN108138276A (en) * | 2015-10-09 | 2018-06-08 | 江阴贝卡尔特钢丝制品有限公司 | With the elongated wire for corrosion resistant metal coating |
| CN108179355A (en) * | 2018-01-31 | 2018-06-19 | 中钢集团郑州金属制品研究院有限公司 | A kind of high-intensity and high-tenacity spring steel wire and its preparation process |
| CN110724795A (en) * | 2019-09-30 | 2020-01-24 | 江苏冠晟超导科技有限公司 | Isothermal quenching heat treatment process of steel wire for wire |
| CN111304537A (en) * | 2020-03-25 | 2020-06-19 | 中国铁道科学研究院集团有限公司 | Strength 2200 MPa-level prestressed steel strand and production process thereof |
| CN113862435A (en) * | 2021-10-09 | 2021-12-31 | 中钢集团郑州金属制品研究院股份有限公司 | Preparation process suitable for high-strength special-shaped spring steel wire |
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| US10570479B2 (en) | 2015-01-30 | 2020-02-25 | Nv Bekaert Sa | High tensile steel wire |
| JP2022523202A (en) * | 2019-02-26 | 2022-04-21 | エンベー ベカルト ソシエテ アノニム | Compression coil springs for actuators to open and close car doors or tailgates |
| KR102355675B1 (en) * | 2019-07-12 | 2022-01-27 | 주식회사 포스코 | High strength steel wire rod and steel wire for spring and manufacturing method same |
| KR102326263B1 (en) * | 2019-12-20 | 2021-11-15 | 주식회사 포스코 | Steel wire rod, steel wire for ultra high strength spring and manufacturing mehtod thereof |
| KR102401440B1 (en) * | 2020-08-28 | 2022-05-24 | 박철옥 | Mask nose wire manufacturing method and iron core manufacturing device for this nose wire |
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| CN108179355A (en) * | 2018-01-31 | 2018-06-19 | 中钢集团郑州金属制品研究院有限公司 | A kind of high-intensity and high-tenacity spring steel wire and its preparation process |
| CN110724795A (en) * | 2019-09-30 | 2020-01-24 | 江苏冠晟超导科技有限公司 | Isothermal quenching heat treatment process of steel wire for wire |
| CN111304537A (en) * | 2020-03-25 | 2020-06-19 | 中国铁道科学研究院集团有限公司 | Strength 2200 MPa-level prestressed steel strand and production process thereof |
| CN113862435A (en) * | 2021-10-09 | 2021-12-31 | 中钢集团郑州金属制品研究院股份有限公司 | Preparation process suitable for high-strength special-shaped spring steel wire |
Also Published As
| Publication number | Publication date |
|---|---|
| HUE034437T2 (en) | 2018-02-28 |
| ES2640626T3 (en) | 2017-11-03 |
| AU2014334010A1 (en) | 2016-03-03 |
| DK3055436T3 (en) | 2017-10-16 |
| MY176216A (en) | 2020-07-24 |
| EP3055436B1 (en) | 2017-08-30 |
| EP3055436A1 (en) | 2016-08-17 |
| PL3055436T3 (en) | 2017-12-29 |
| BR112016007217A2 (en) | 2017-08-01 |
| WO2015052035A1 (en) | 2015-04-16 |
| ZA201601568B (en) | 2017-09-27 |
| KR20160068765A (en) | 2016-06-15 |
| US20160237518A1 (en) | 2016-08-18 |
| HRP20171447T1 (en) | 2018-01-12 |
| PT3055436T (en) | 2017-09-13 |
| SI3055436T1 (en) | 2017-11-30 |
| RS56504B1 (en) | 2018-02-28 |
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