TWI523956B - Metal parts for buckle parts and zippers for use, and manufacturing methods for metal parts for buckles - Google Patents

Description

Metal parts for buckles, zippers using the same, and metal parts for fastening parts

The present invention relates to a metal part for a fastening member of a zipper mounted on a garment for detecting a needle or the like, and a zipper using the same, and a method for manufacturing a metal part for a fastening member, in particular, One is to provide a non-magnetic material that is not detected by the needle detector, and to improve the workability of the metal parts for the fastening member to improve the production efficiency.

In order to prevent the malfunction of the needle detector due to the misuse of a dangerous object such as a needle, the zipper attached to the clothes using the needle detector must be almost unaffected by the magnetic field without being magnetized. The non-magnetic metal material is used for detecting the needles, broken needles and other needles which are mixed in the sewing stage.

Here, in the case of a part requiring corrosion resistance and non-magnetic properties, a Worstian iron-based stainless steel represented by SUS304 is generally used. For example, Patent Document 1 describes a high Mn and a high content of Mn and N. N-series stainless steel is used as a high corrosion resistant, high strength, non-magnetic stainless steel.

In addition, in the case of the patent document 2, in order to accurately detect the mixing of the broken needle at the time of sewing by the stainless steel used for a zipper, etc., the following stainless steel which responds to a needle detector is provided: It is satisfy|filled by the mass %. C: 0.01 to 0.15%, Si: 0.1 to 5%, Mn: 1 to 10%, Ni: 8 to 25%, Cr: 14 to 30%, N: 0.01 to less than 0.06%, and the balance containing Fe and impurities And is defined as a composition having a Ni equivalent value of Ni equivalent = Ni + 0.6 Mn + 9.69 (C + N) + 0.18 Cr - 0.11 Si ² of 19 or more, and a magnetic permeability in a magnetic field of 1 kOe is 1.005 or less, 18 kOe The magnetization in the magnetic field is below 550 memu/g, which in turn shows Needle performance below 1.2mm iron ball.

[Previous Technical Literature] [Patent Literature]

Patent Document 1: Japanese Patent Laid-Open No. 2011-6776

Patent Document 2: Japanese Patent No. 3947679

However, in the stainless steel described in Patent Document 1, when it is processed, a very small amount of processing is induced to induce the transition of the granulated iron and the magnetic properties are low. Therefore, in the stainless steel, for example, a magnetic field of 10,000 Oersted is not obtained. The magnetic flux density is non-magnetic, so-called super non-magnetic, to the extent of 0.01 T or less. Therefore, when a zipper is used and a needle detector is used for the clothes having the zipper, the zipper is detected by the needle detector. And caused the wrong action.

Further, in the stainless steel described in Patent Document 2, when the hardness is excessively high, and in particular, when a plurality of fastener elements constituting the fastener element row of the fastener are made of the stainless steel, it is difficult to continuously make the fastener elements continuous. Since it is formed, it is necessary to reduce the manufacturing efficiency, and in addition to this problem, there is even a concern that the forming mold is broken. The stainless steel can be reduced in hardness by, for example, performing a plurality of heat treatments, so that continuous formation of the fastener elements can be achieved. However, in this case, there are other problems such as an increase in manufacturing cost due to the implementation of the heat treatment.

An object of the present invention is to solve the problems of the prior art, and an object of the invention is to provide a metal part for a fastening member, a zipper using the same, and a manufacturing method of a metal part for a fastening member, the metal part for the fastening component having Non-magnetic, which does not cause the malfunction of the needle detector, suppresses the manufacturing cost relatively small and improves productivity.

The metal parts for the fastening component of the present invention are C% by weight or less, and contain C: 0.08% or less. Si: 0.05% to 2.0%, Mn: more than 8.0% and 25.0% or less, P: 0.06% or less, S: 0.01% or less, Ni: more than 6.0% and 30.0% or less, Cr: 13.0% to 25.0%, Cu: 0.2%~5.0%, N: less than 0.20%, Al: 0.002~1.5%, and C+N is less than 0.20%, the remainder contains Fe and unavoidable impurities, and will be represented by the following formula (a) Md30 is set to -150 or less, Md30=413-462(C+N)-9.2Si-8.1Mn-9.5Ni-13.7Cr-29Cu (a)

Here, the element symbol in the formula (a) means the content (% by mass) of the element in the metal part for the fastening member.

Here, in the present invention, as the needle detecting performance, the iron ball value of the chain and the zipper is preferably 1.5mm or less, in addition, as a zipper element, or a stop block (material) such as an upper and lower stop, an opening and closing member, the magnetic body is displayed when the component is placed in a magnetic field of 10,000 Oe. The pass density is 0.01 T or less, and particularly preferably 0.007 T or less.

Further, the metal parts for the fastening members of the present invention are preferably formed by cold working, cold working, and heat treatment.

In the metal part for the fastening member of the present invention, it is possible to further contain 3.0% or less of Mo by mass%. In this case, it is preferable to replace the Md30 represented by the above formula (a) with the following formula. (b) The indicated Md30' is set to -150 or less, and Md30' = 413-462 (C+N)-9.2Si-8.1Mn-9.5Ni-13.7Cr-18.5Mo-29Cu (b).

The metal component for the fastening member may be at least one selected from the group consisting of Nb, V, Ti, W, and Ta in an amount of 1.0% by mass or less.

In addition, it is possible to further contain, in mass%, 3.0% or less of Co, and/or, in mass%, 0.01% or less of B.

In addition, it may further contain one or more selected from the group consisting of Ca: 0.01% or less, Mg: 0.01% or less, and REM: 0.05% or less in mass%.

Further, the zipper of the present invention includes a fastener component, and the fastener component comprises a pair of sprocket teeth arranged side by side, and in order to mesh the sprocket teeth of the sprocket row Or a sliding member that is slidably displaced along the sprocket row, and wherein each of the fastener elements of the fastener component forming part is made of a metal part of any of the fastening members previously described.

Further, in the method of manufacturing a metal part for a fastening member according to the present invention, when manufacturing the metal part for the fastening member, cold processing (wire drawing) is performed on a wire or a steel wire (for example, a round wire) having a specific composition. And the wire or the steel wire is formed into a processed material (a metal wire described later) including, for example, a profiled line having a substantially Y-shaped cross-sectional shape and/or a rectangular line having a rectangular cross-sectional shape. Thereafter, the processed material is subjected to cold working (cutting processing, press working, etc.).

Here, it is preferable that the cross-sectional hardness of the processed material is 220 to 360 in terms of Vickers hardness HV measured according to the Vickers hardness test of JIS Z2244, and the elongation of the processed material is measured according to the tensile test of JIS Z2241. It is 1% or more and the tensile strength is in the range of 450 MPa to 1100 MPa.

According to the present invention, the composition of the metal part for the fastening member is set to be the above, and the Md30 represented by the formula (a) is set to -150 or less, so that it is not detected by the needle detector. Non-magnetic, and, compared with the prior art stainless steel, the hardness after cold working is relatively small, so especially when the metal parts of the fastening parts are made into fastener elements, the chain can be realized without performing multiple heat treatments. As a result of the continuous formation of the teeth, it is easy to process the metal parts for the fastening members, and the manufacturing cost is not increased by performing the plurality of heat treatments, and the manufacturing efficiency can be greatly improved.

1‧‧‧ zipper

2‧‧‧Chain row

2a‧‧‧ sprocket

2b‧‧‧ buckled head

2c‧‧‧foot

3‧‧‧Chain

3a‧‧‧ core

4‧‧‧Sliding parts

5‧‧‧Upstop

6‧‧‧Next stop

12‧‧‧Special line for chain teeth

12a‧‧‧ sprocket forming member

15‧‧‧Headline for upper stop

15a‧‧‧Upper stop forming member

16‧‧‧Shaped line for lower stop

16a‧‧‧Bottom stop forming member

51‧‧‧1st side

51B‧‧‧1st side

51C‧‧‧ side

51a‧‧‧1st straight line

51b‧‧‧1st member

51c‧‧‧2nd member

52‧‧‧2nd side

52B‧‧‧2nd side

52C‧‧‧ side

52a‧‧‧2nd straight line

52b‧‧‧1st member

52c‧‧‧2nd member

53‧‧‧3rd side

53C‧‧‧ side

54‧‧‧4th side

54C‧‧‧ side

71‧‧‧1st diagonal

72‧‧‧2nd diagonal

73‧‧‧ central location

80B‧‧‧1st side

80b‧‧‧1st member

80c‧‧‧2nd member

91a‧‧‧1st straight line

91b‧‧‧Scope of contact

91c‧‧‧Scope of contact

92a‧‧‧2nd straight line

92b‧‧‧Scope of contact

92c‧‧‧Scope of contact

C1‧‧‧ recess

C2‧‧‧ recess

D1‧‧‧ size

L1‧‧‧ length

L1b‧‧‧ length

L1c‧‧‧ length

L2‧‧‧ length

L2b‧‧‧ length

L2c‧‧‧ length

L91a‧‧‧ length

L91b‧‧‧ length

L91c‧‧‧ length

L92a‧‧‧ length

L92b‧‧‧ length

L92c‧‧‧ length

LC1‧‧‧Width size

LC2‧‧‧Width size

T‧‧‧1st size

W‧‧‧2nd size

‧‧‧‧ angle

Θ‧‧‧ angle

Fig. 1 is a front elevational view showing a zipper having a metal part for a fastening member according to an embodiment of the present invention.

Figure 2 is a perspective view showing a step of forming the sprocket, the upper stop and the lower stop of the zipper of Figure 1 on the chain cloth.

Fig. 3 is a cross-sectional view showing a steel wire which can be used for the manufacture of a metal part for a fastening member.

4(a)-(c) are cross-sectional views showing other steel wires which can be used for the manufacture of metal parts for fastening members.

Fig. 5 is a cross-sectional view showing another steel wire which can be used for the manufacture of a metal part for a fastening member.

Fig. 6 is a plan view showing the needle detector of the needle test of the embodiment.

Hereinafter, embodiments of the present invention will be described in detail with reference to the drawings.

The slide fastener 1 illustrated in Fig. 1 includes a pair of right and left fastener element rows 2, in which a plurality of fastener elements 2a are arranged side by side in the vertical direction in the drawing, and a chain cloth 3 including a cloth or the like and having the same Each of the sprocket 2a of the sprocket row 2 extends upwardly from the upper side of the figure to form a relatively thick rope-like core portion 3a; and a slider 4 with a pull tab, the inside of which is inserted into each of the sprocket rows 2, In order to cause the respective sprocket 2a of the pair of sprocket rows 2 to mesh or disengage with each other, it is slidably displaced in the extending direction of the sprocket row 2 (up and down direction in the drawing) and is held, for example, by a user.

Here, in the zipper 1, at one end portion (the upper end portion in FIG. 1) of the element row 2, it is provided to prevent the pair of element rows 2 from being opened and closed by the meshing and separation of the fastener elements 2a. a further displaced upper stop 5 of the slider 4 in the direction of the closed chain of teeth 2, and at the other end of the element row 2 (lower end in Fig. 1), is provided to block the slider 4 A further displaced lower stop 6 in the direction of the chain rows 2 is opened, by which the range of movement of the slider 4 is limited.

Here, in the present invention, at least one of the fastener elements 2a, the slider 4, the upper and lower stoppers 5, 6 of the fastener element row 2 of the zipper 1, and other fastening members which can be formed of a metal material are formed. The component forming member, in particular, each of the fastener elements 2a is made of a metal member including a fastening member of the following Worstian iron-based stainless steel. Preferably, at least one of the metal parts for the other fastening members, such as the slider 4, the upper stopper 5, and the lower stopper 6, is also formed of the Vostian iron-based stainless steel.

According to the above, when the needle attached to the zipper 1 is used for the detection of other needles such as needles by the needle detector, the inherent properties of the Wostian iron-based stainless steel which is a metal part for forming the fastening member are exceeded. Non-magnetic, it can be advantageously eliminated that the needle detector erroneously detects the buckle as a needle.

Further, since the Worsfield iron-based stainless steel has a smaller hardness after cold working than the conventional stainless steel described in Patent Document 1, it can be easily processed without performing a plurality of heat treatments, and therefore, when the fastener is manufactured, In the case of metal parts, manufacturing efficiency can be improved at a relatively small manufacturing cost.

Further, the Vostian iron-based stainless steel constituting the metal part for the fastening material of the present invention contains C: 0.08% or less, Si: 0.05% to 2.0%, and Mn: more than 8.0% and 25.0% or less, by mass%. P: 0.06% or less, S: 0.01% or less, Ni: more than 6.0% and 30.0% or less, Cr: 13.0% to 25.0%, Cu: 0.2% to 5.0%, N: less than 0.20%, and Al: 0.002 to 1.5 %, and C+N is less than 0.20%, the remainder contains Fe and unavoidable impurities, and Md30 represented by formula (a) is set to -150 or less, and formula (a): Md30 = 413-462 (C+ N)-9.2Si-8.1Mn-9.5Ni-13.7Cr-29Cu.

In the Vostian iron-based stainless steel, by reducing the Md30 represented by the formula (a) as described above, the stability of the Worthite iron system is greatly improved, even in the case of forming a complicated shape for cold working. At the time, it is also possible to completely suppress the generation of the iron field in the field by the processing of the magnetic body. Further, by reducing the contents of C and N and containing Cu or Al in the above range, work hardening can be suppressed, and the required cold workability can be ensured. Further, by setting the contents of Mn and Ni within the above range, the magnetic properties of the base of the non-magnetic material can be further reduced, and super-non-magnetic properties can be obtained.

(addition amount of each component)

When C is added in excess of 0.08%, the strength is increased and the cold workability is deteriorated. Therefore, the upper limit is made 0.08%, preferably 0.05% or less. On the other hand, if you excessively reduce the inclusion of C The amount causes an increase in the production cost, so the lower limit is preferably set to 0.001%, and the content of C is particularly preferably 0.01% or more. The content of C is preferably in the range of 0.01 to 0.05%.

The Si system is added in an amount of 0.05% or more for deoxidation, and preferably 0.1% or more. However, when Si is added in excess of 2.0%, cold workability is deteriorated. Therefore, the upper limit of the Si content is set to 2.0%, preferably 1.0% or less. The Si content is preferably in the range of 0.1 to 1.0%.

Mn is added in an amount of more than 8.0%, preferably more than 13.0%, in order to drastically improve the stability of the Worstian iron after cold working and obtain super-non-magnetic properties. However, when Mn is added in excess of 25.0%, the effect is saturated, the strength is increased, and the cold workability is deteriorated. Therefore, the upper limit of the Mn content is 25.0%, preferably 20.0% or less, and more preferably less than 16.0%. The preferred range of Mn content is greater than 13.0% and less than 20%. The Mn content is further preferably less than 16.0%.

The content of P is set to 0.06% or less, preferably 0.04% or less, in order to ensure cold workability. However, it is difficult to industrially set the content of P to zero, so the preferred range is 0.01% to 0.04%.

The content of S is set to 0.01% or less, preferably 0.005% or less, in order to secure the thermal manufacturability and corrosion resistance of the wire. However, it is difficult to industrially set the content of S to zero, so the preferred range is 0.0002 to 0.005%.

Ni is preferably added in an amount of more than 6.0% in order to drastically increase the stability of the Worth iron after cold working and to ensure super-non-magnetic properties, and it is preferable to add 8.0% or more. However, when Ni is added in excess of 30.0%, even if it is non-magnetic under the Vostian iron system, the number of atomic bonds of Fe-Ni increases as in the case of a nickel steel alloy, and exhibits weak magnetic properties. Therefore, the upper limit of the Ni content is 30.0%, preferably 20.0% or less, and more preferably less than 10.0%. Since it is preferred to minimize the atomic bonding of the Fe-Ni pair, the Ni content is preferably in the range of 8.0% or more and less than 10.0%.

Cr is added in an amount of 13.0% or more, preferably 15.0%, in order to drastically improve the stability of the Worstian iron after cold working and to ensure super non-magnetic properties, thereby obtaining high corrosion resistance. on. However, when Cr is added in an amount of more than 25.0%, δ (delta)-fertilizer iron of a bcc structure of a ferromagnetic material is generated in one part of the structure, so that magnetic properties are exhibited and strength is increased, and cold workability is lowered. Therefore, the upper limit of the Cr content is 25.0%, preferably 20.0% or less. The preferred range of Cr content is from 15.0% to 20.0%.

Cu is added in an amount of 0.2% or more in order to drastically improve the stability of the Worstian iron after cold working and to ensure super non-magnetic properties, and to suppress work hardening of the Worthite iron and to ensure cold workability. Cu is preferably added in an amount of 1.0% or more, and more preferably added in an amount of more than 3.0%. However, when Cu is added in excess of 5.0%, thermal cracking occurs due to significant solidification segregation of Cu, so that it cannot be industrially produced. Therefore, the upper limit of the Cu content is set to 5.0%, preferably 4.0% or less. It is preferable to set the Cu content to 1.0% to 4.0%, and more preferably to be more than 3.0% and 4.0% or less.

In the case of N, when 0.20% or more is added, the strength is increased and the cold workability is deteriorated. Therefore, the content of N is set to be less than 0.20%, preferably less than 0.10%. On the other hand, excessively reducing the content of N causes an increase in the production cost. Therefore, the content of N is preferably 0.001% or more, and more preferably 0.01% or more. A preferred range of the content of N is 0.01 or more and less than 0.10%.

In addition to the Cu, the Al-based deoxidizing element is an important element for ensuring cold workability in order to suppress work hardening of the Worthite iron, and is preferably contained in an amount of 0.002% or more, preferably 0.01% or more. . However, when Al is added in excess of 1.5%, the effect is saturated, and coarse interfacial substances are generated, and the cold workability is rather deteriorated. Therefore, the upper limit of the Al content is set to 1.5%, preferably 1.3% or less, and more preferably 1.2% or less. The preferred range of Al content is from 0.01% to 1.2%.

The C+N system is limited to less than 0.20% in order to ensure the soft workability of the complicated shape parts in order to soften it. The content of C+N is preferably 0.10% or less.

The Md30 in the above formula (a) is an index obtained by investigating the relationship between the amount of iron in the field and the composition of the processing after the cold working, and is based on the stretching of the single phase of the Vostian iron. The 50% metamorphosis of the time-varying tissue is the temperature of the granulated iron. The smaller the value of Md30, the more stable the Worthite iron is, and the production of the granulated iron is suppressed. Therefore, in order to ensure super non-magnetic properties of the wire, it is necessary to control the Md30 value. In order to make it super non-magnetic after cold working, Md30 must be controlled below -150. Md30 is preferably set to -170 or less, and more preferably -200 or less.

The unavoidable impurities are, for example, O: 0.001 to 0.01%, Zr: 0.0001 to 0.01, Sn: 0.001 to 0.1, Pb: 0.00005 to 0.01%, Bi: 0.00005 to 0.01%, and Zn mixed in the production of ordinary stainless steel. : A material contained in a raw material or a refractory such as 0.0005 to 0.01%.

In the case of Mo, in order to improve the corrosion resistance of the product, it is preferably added in an amount of preferably 0.01% or more, more preferably 0.2% or more, as needed. However, when Mo is added in excess of 3.0%, the strength becomes high, and there is a possibility that the cold workability is lowered. Therefore, the upper limit of the Mo content can be set to 3.0%, preferably 2.0%. A particularly preferable range of Mo content is 0.2 to 2.0%.

Further, when Mo is contained, Md30' calculated by the following formula (b) is used instead of the above formula (a), and Md30' obtained by the formula (b) is preferably set to -150 or less. .

Formula (b): Md30'=413-462(C+N)-9.2Si-8.1Mn-9.5Ni-13.7Cr-18.5Mo-29Cu

In order to form a nitrogen carbide to improve corrosion resistance, Nb, V, Ti, W, and Ta may be added in one type or more as needed. When one or more of Nb, V, Ti, W, and Ta are contained, the content of each element is preferably 0.01% or more, and more preferably 0.05% or more. When these elements are added in excess of 1.0%, a coarse intervening substance is produced, and there is a possibility that the cold workability is lowered. Therefore, the upper limit of the content of each of Nb, V, Ti, W, and Ta can be set to 1.0%, preferably 0.6% or less. The content of each element is preferably in the range of 0.05 to 0.6%.

In order to drastically improve the stability of the Worstian iron after cold working and to obtain super non-magnetic properties, the Co is preferably added in an amount of preferably 0.05% or more, more preferably 0.2% or more. however, When Co is added in excess of 3.0%, the strength is increased, and there is a possibility that the cold workability is deteriorated. Therefore, the content of Co is preferably set to an upper limit of 3.0%, and more preferably set to 1.0% or less. The content of Co is particularly preferably in the range of 0.2 to 1.0%.

In order to improve the heat manufacturability, B may be added in an amount of 0.0005% or more, preferably 0.001% or more. However, when B is added in excess of 0.015%, boride is generated instead, and the cold workability may be lowered. Therefore, the upper limit of the content of B can be set to 0.015%, preferably 0.01% or less. The content of B is preferably in the range of 0.001% to 0.01%.

Ca, Mg, and REM are elements which are effective for deoxidation, and one or more of these elements may be added as needed. However, if excessively added, soft magnetic properties are deteriorated, and coarse deoxidation products are generated, whereby cold workability may be lowered. Sex. Therefore, when Ca is contained, the content thereof is made 0.01% or less, preferably 0.004% or less. When Mg is contained, the content thereof is made 0.01% or less, preferably 0.0015% or less. In the case of containing REM, the content thereof is made 0.05% or less, preferably 0.01% or less. Further, a preferred lower limit of the Ca content is 0.0005%, more preferably 0.001%. A preferred lower limit of the Mg content is 0.0005%, more preferably 0.0006%. A preferred lower limit of the REM content is 0.0005%, more preferably 0.001%. The preferred range of the content of each of the elements is Ca: 0.001 to 0.004%, Mg: 0.0006 to 0.0015%, and REM: 0.001 to 0.01%.

(Stretching strength of tensile strength and tensile reduction of tensile section)

The tensile strength of the wire of the Vostian iron-based stainless steel for forming the metal part for the fastening member of the present invention can be 650 MPa or less, especially 590 MPa or less, and the tensile reduction ratio of the original wire can be set. It is 70% or more, especially 75% or more. When the tensile strength of the original wire is 650 MPa or less, the cold workability is good. Moreover, when the shrinkage ratio of the tensile section of the original wire is 70% or more, the cold workability is good.

These mechanical properties can be further improved by more strictly controlling the composition of the steel according to the cold workability required to be set.

That is, the composition of the composition is controlled to be Mn: more than 13.0% and less than 20%, and Cu: 1.0%. When the ratio is ~4.0%, Al: 0.01% to 1.3%, and N: 0.01 or more and less than 0.10%, the tensile strength is 590 MPa or less, and the tensile strength at a tensile reduction of the surface is 75% or more. Thereby, the cold workability of the wire is further improved.

(needle performance)

The needle detection performance is equivalent to a static magnetic field type needle detector that measures the amount of change in the magnetic flux density generated when the metal passes through the magnetic flux at a constant speed. The amount of change in the magnetic flux density of the 1.5 mm iron ball is set to 100 as a reference value (indicative value), and the value of the needle to be measured when measuring the object to be measured is evaluated based on the relative value with respect to the above reference value. In other words, if the needle value of the object to be measured is equal to or less than the reference value, the iron ball value becomes 1.5mm or less. Also, whether the needle detection performance is equivalent Indicates that any of the iron ball values of 0.8, 1.2, and 1.5 mm is below the value of the iron ball. In the case of 0.8mm or less, it means that the smallest special size broken needle used in sewing can also be detected. In the case of 1.5 mm or less, it means that the broken needle of the commonly used size can be sufficiently detected.

Moreover, in the present invention, it is preferred to have an iron value Needle performance below 1.5mm, better Below 1.2mm, especially best 0.8mm or less. Here, the object to be measured is a chain, and the needle value of the object to be measured is obtained by moving it perpendicularly to the direction in which the needle detector is moved.

(flux density)

In the present invention, for example, when one element 2a is disposed in a magnetic field of 10,000 Oe (Oe), it is preferable that one of the elements has a magnetic flux density of 0.01 T or less. More preferably, the magnetic flux density in the same magnetic field of 10,000 Oe is less than 0.007T. The same applies to the magnetic flux density of the stoppers such as the upper and lower stoppers 5, 6 or the opening and closing members.

(Production method)

The metal parts for the fastening members described above can be manufactured by the method described below.

First, the slab having the composition as described above is reduced by a rate of 99% or more. The wire rod is hot-rolled, and thereafter, a homogenization heat treatment is performed at 1000 to 1200 ° C to obtain a wire.

Further, in the wire rolling of the small diameter, unlike the thin plate, the thick plate, the steel pipe, and the rod rolling, strong heat processing can be performed. The hot rolling between the wires and the homogenization heat treatment are effective for homogenizing the wires and for super-nonmagnetic stabilization. In particular, in order to obtain a soft, ultra-non-magnetic wire material after cold working, it is necessary to heat the wire between the slabs having the above-mentioned composition and the extremely high reduction ratio of 99% or more, and then to 1000~ The homogenization heat treatment was carried out at 1200 °C.

Here, if the total reduction ratio in the thermal compression of the wire is less than 99%, the homogenization of the material is insufficient, and it is difficult to obtain super-nonmagnetic. Therefore, the shrinkage ratio in the hot rolling of the wire is set to 99% or more, preferably 99.5 to 99.99%.

In addition, when the homogenization heat treatment temperature after the hot rolling of the wire is less than 1000 ° C, the strength is high and the cold workability is deteriorated, and the homogenization is insufficient, so that the super non-magnetic property is also deteriorated. Therefore, the homogenization heat treatment temperature is set to 1000 ° C or higher, preferably 1050 ° C or higher. On the other hand, if the homogenization heat treatment temperature exceeds 1200 ° C, the ferromagnetic iron phase of the ferromagnetic phase is precipitated, so that the super non-magnetic property is deteriorated. Therefore, the homogenization heat treatment temperature can be 1200 ° C or lower, preferably 1 150 ° C or lower. The range of the homogenization heat treatment temperature can be set to 1000 to 1200 ° C, preferably 1000 to 1150 ° C.

In this way, the reduction ratio in the rolling of the wire for performing the hot working and the subsequent uniform heat treatment conditions are specified, and the segregation of a small amount of the alloy is reduced, thereby being ultra-nonmagnetic stable.

Then, the wire is subjected to cold working to form the wire into a processed material including a rectangular wire and/or a profiled wire, and thereafter, the processed material is subjected to cold working, whereby a metal component for the fastening member can be manufactured.

Here, during the cold working such as rolling of the processed material, the processed material may be subjected to a heat treatment such as annealing, that is, an intermediate heat treatment performed during the rolling, whereby the hardness may be lowered to further improve the workability. The heat treatment performed here is preferably carried out in accordance with the above uniform heating Handle the same processing.

Here, in terms of continuous molding of a fastener element or the like as a metal member for a fastening member, it is preferable that the hardness of the processing material is set to be 220 to 360 in terms of Vickers hardness HV. In the range, the tensile strength is in the range of 450 MPa to 1100 MPa, and the elongation of the processed material is set to 1% or more. In this case, when the hardness HV of the processed material is less than 220 or the tensile strength is 450 MPa or less, the material deformation during the forming of the fastener element is large, and the high-precision machining to a specific shape becomes difficult. When the hardness HV of the processed material exceeds 360, or the strength is greater than 1100 MPa, or the elongation is less than 1%, continuous formation of the fastener elements is difficult.

In order to suppress the premature breakage of the molding die for performing the zipper element implantation and to further stabilize the accuracy of the zipper tooth insertion molding, it is preferable to set the Vickers hardness HV of the processing material to 220 to 310. Further, the tensile strength is more preferably 700 to 800 MPa.

Further, each of the sprocket 2a constituting the element row 2 of the slide fastener 1 is formed of a metal material and has a cross-sectional shape as a processing material in a substantially Y-shape over the entire length as shown in FIG. The profiled wire 12 for the sprocket is cut at a specific length, and is set as the sprocket forming member 12a. Then, the sprocket forming member 12a is subjected to press working, thereby forming engagement with the other sprocket 2a in use. The head portion 2b is fastened, and then the leg portion 2c is placed in a state in which the core portion 3a of the chain cloth 3 is disposed between the two leg portions 2c extending in the Y-shaped sprocket forming member 12a. Plastic deformation is performed toward the inner side, and the core portion 3a is sandwiched between the leg portions 2c and pressed, whereby the core portion 3a can be attached to the chain fabric 3.

Here, especially when the fastener element 2 formed as described above in the fastening component forming member of the zipper 1 illustrated in FIG. 1 is composed of the metal component of the fastening component mentioned in the present invention, the fastening component Since the hardness of the Worstian iron-based stainless steel having a metal part is relatively small, the sprocket 2a can be continuously formed by the sprocket forming and mounting machine, so that the manufacturing efficiency can be drastically improved. Furthermore, a plurality of annealings may be performed when the profiled line 12 is formed. The heat treatment is carried out, but the continuous formation of the fastener elements 2a can be carried out even without such heat treatment, so that the increase in cost due to the heat treatment can be prevented.

The upper stop 5 or the lower stop 6, the slider 4, and the like can be formed of a fastening member formed of a metal material from the viewpoint of more effectively preventing the malfunction of the needle detector due to the zipper 1 and further improving the manufacturing efficiency. The part is also preferably constructed of metal parts of the fastening member of the present invention.

Further, for example, the upper stopper 5 is formed by cutting a rectangular wire 15 for a flat upper stopper as a processing material as shown in FIG. 2 by a specific length and plastically deforming it into a U shape. The upper stopper forming member 15a is press-fixed with respect to the chain cloth 3 with the core portion 3a interposed therebetween, whereby the upper stopper forming member 15a can be formed on the fastener fabric 3. Further, the lower stopper 6 is cut by a specific length by cutting the profiled line 16 for the lower stopper having the cross-sectional shape of the two U-shaped portions as shown in FIG. The stopper forming member 16a is pressed and fixed to the respective link fabrics 3, whereby the attachment can be performed. However, the upper stop 5 and the lower stop 6 are not limited to the above-described forming method. For example, the upper stop 5 may be formed by a profile line and the lower stop 6 may be formed by a rectangular line.

Although not shown in the drawings, the slider 4 shown in the figure is formed by pressing a long strip having a rectangular plate shape in a plurality of stages and cutting at a predetermined interval to form a slider main body. It is a combination of wire springs and pull tabs. Further, the pull tab can be formed by punching a specific shape from a plate-like body having a rectangular cross section.

Further, when manufacturing the metal parts for the fastening members of the present invention, it is also possible to use a steel wire obtained by drawing the above-mentioned wires into a wire. This steel wire system is set to have the same composition and Md30 value as the above-mentioned wire material, thereby exhibiting super non-magnetic properties.

In order to ensure cold workability, the steel wire preferably has a tensile strength of 650 MPa or less and a tensile reduction ratio of 70% or more. The characteristics of such a steel wire can be obtained by using the above-mentioned wire as a material.

Further, the steel wire system is controlled to have a composition of Mn: more than 13.0% and 20% or less, Cu: 1.0% to 4.0%, Al: 0.01% to 1.3%, and N: 0.01%, similarly to the steel wire. When the amount is less than 0.10%, the tensile strength is 590 MPa or less, and the tensile reduction ratio of the tensile section is 75% or more. By forming such a steel wire, the cold workability is further improved.

In addition, Ni or Cu affects the magnetic properties of the paramagnetic steel. When the standard deviation σ of the unevenness of the Ni concentration in the central portion of the cross section of the wire or the steel wire is 5% or less, and the standard deviation σ of the unevenness of the Cu concentration is 1.5% or less, the local magnetic property can be suppressed to be high. Since the formation of the place, the super non-magnetic property can be stably obtained. Therefore, it is preferable to set the standard deviation σ of the unevenness of the Ni concentration to 5% or less, and to set the standard deviation σ of the unevenness of the Cu concentration to 1.5% or less. More preferably, the standard deviation σ of the unevenness of the Ni concentration is 3% or less, and the standard deviation σ of the unevenness of the Cu concentration is 1.0% or less.

Further, the standard deviation σ of the unevenness of the Ni concentration or the Cu concentration in the central portion of the cross section of the wire or the steel wire is based on an EPMA (Electron Probe Micro Analyzer) for any portion of the central portion of the cross section of the wire or the steel wire. The electron probe microanalyzer was used to analyze the results obtained by performing graph analysis on the Ni concentration and the Cu concentration.

Here, the central region of the cross section of the wire or the steel wire is surrounded by a circle having a radius of 1/4 of the diameter of the wire or steel wire from the center when the cross-sectional shape is circular. Area. Further, in the case where the cross-sectional shape is a regular polygon having 4 or more sides, it means a region surrounded by a circle having a radius of 1/4 of the diagonal line passing through the center from the center. Further, in the case where the cross-sectional shape is a shape having a profiled cross-sectional shape as shown in Figs. 3 to 5 in which the following steel wire loop fastener is formed, it means the following region. First, the first diagonal line 71 including a straight line connecting one end of the first straight portion 51a (91a) and the end portion of the second straight portion 52a (92a) away from the end of the first straight portion 51a (91a) is drawn. . Further, the drawing includes a second diagonal line connecting the other end of the first straight portion 51a (91a) and the end portion of the second straight portion 52a (92a) away from the other end of the first straight portion 51a (91a). Line 72. Then, the first diagonal line is centered on the center position 73 in the longitudinal direction of the shorter one of the first diagonal 71 and the second diagonal 72 (the second diagonal 72 in FIG. 3). 1/4 of the length of the shorter of 71 and the second diagonal 72 is set to a radius r, and a region surrounded by the circle having a radius r is set as a cross section. Central area.

The method for producing the above steel wire is not particularly limited, and a usual method can be used. The method for producing a normal steel wire includes, for example, a step of stretching a steel wire at a linear ratio of 10 to 95%, and a strand annealing at 900 to 1200 ° C for 5 seconds to 24 hours. The method of the step.

In order to improve the dimensional accuracy of the steel wire, the wire drawing ratio of the steel wire is preferably 10% or more, more preferably 20% or more. Further, in order to prevent breakage in the stretched wire, the wire drawing ratio of the steel wire is preferably 95% or less, more preferably 90% or less.

In order to eliminate the strain due to the step of stretching, the temperature of the strand annealing is preferably 900 ° C or higher, more preferably 1000 ° C or higher. Further, in order to prevent the precipitation of the ferromagnetic iron phase of the ferromagnetic material, the temperature of the strand annealing is preferably 1200 ° C or lower, more preferably 1150 ° C or lower.

In order to obtain a sufficient annealing effect, the annealing time of the strand annealing is preferably 5 seconds or longer, more preferably 20 seconds or longer. Further, in order to improve productivity, the annealing time of the strand annealing is preferably 24 hours or shorter, more preferably 1 hour or shorter.

The cross-sectional shape of the steel wire is not particularly limited, and may be a circular shape or a polygonal cross-sectional shape such as a polygonal shape. In the case where the steel wire has a profiled cross-sectional shape, it is preferably a cross-sectional shape as described below in order to prevent deformation of the cross-sectional shape due to winding after the strand annealing.

A steel wire loop can be formed by winding a steel wire having a specific cross-sectional shape as described above under specific conditions.

In order to be machined into a complex shape from a steel wire, it is preferred to have a near net shaper near the shape of the final product at the stage of the steel wire. However, when the steel wire is processed into a profile shape of a near-net shape, if the wire is subjected to a wire drawing process to form a steel wire having a profiled cross-sectional shape, and after being subjected to a strand annealing, the steel is wound. The possibility that the profile of the line is destroyed. Therefore, the steel wire is preferably formed into a cross-sectional shape as shown below, even if it is wound after being subjected to stranding annealing in order to form a steel wire loop.

Figure 3 is a cross-sectional view for explaining the cross-sectional shape of a steel wire wound around a steel wire loop Figure. The cross-sectional shape shown in FIG. 3 is a rectangle, and includes the first side 51 having the first straight portion 51a and the first straight portion 51a inclined at an angle (α) of 30 or less with respect to the first straight portion 51a. The linear portion 51a faces the second side 52 of the second straight portion 52a disposed, and includes a third side of a straight line connecting one end of the first side 51 and the end of the second side 52 close to one end of the first side 51. 53. A fourth side 54 including a straight line connecting the other end of the first side 51 and the other end of the second side 52 close to the other end of the first side 51.

In the cross-sectional shape shown in FIG. 3, the angle α between the extending direction of the first straight portion 51a and the extending direction of the second straight portion 52a is 30 or less. In the portion illustrated in FIG. 3, the second straight portion 52a is disposed at an angle inclined with respect to the first straight portion 51a, but the second straight portion 52a of the second side 52 may be parallel to the first straight portion 51a.

Usually, the steel wire of the profiled cross-sectional shape obtained by performing the wire drawing process on the wire is subjected to a strand annealing. The steel wire after the strand annealing is conveyed in a specific conveying direction by a pinch roller having a pair of oppositely disposed rolls, and is conveyed to a cylindrical drum wound by a steel wire for winding. The coiled steel wire is unloaded from the cylindrical drum and is released from the tension when it is taken up, and becomes a steel wire loop buckle.

In the cross-sectional shape shown in FIG. 3, when the angle α between the extending direction of the first straight portion 51a and the extending direction of the second straight portion 52a exceeds 30°, in the method of manufacturing the steel wire loop described below When the pair of rollers in which the pinch rolls are disposed in the opposite direction are brought into contact with the first straight portion 51a and the second straight portion 52a, and the steel wire passes between the pair of the pinch rolls, the pin is fed. The stress of the roller is concentrated on the apex portion of the rectangle in the cross-sectional shape of the steel wire. As a result, there is a case where the apex portion of the cross-sectional shape of the steel wire is broken or deformed or the steel wire is broken.

In addition, when the angle α of the above configuration is more than 30°, it is difficult to make the respective roller pairs of the pinch rolls contact the first straight portion 51a and the second straight portion 52a, and the state in which the steel wire is sandwiched between the pair of rollers becomes not stable. Therefore, even if the steel wire passes through the pinch roller, the control function in the conveying direction of the steel wire of the pinch roller cannot be sufficiently obtained.

In addition, when the angle α of the above-described configuration is more than 30°, the first straight portion 51a and the second straight portion 52a which are wound around the adjacent steel wire of the cylindrical drum are unlikely to be in surface contact. As a result, the adjacent steel wires wound around the cylindrical drum are in a state of being in point contact when they are easily observed in cross section. When the adjacent steel wires are wound in contact with each other when viewed in a cross section, there is a case where the portion where the steel wire is in contact with the wire is broken due to the tension at the time of winding, and the steel wire is broken.

Further, when the angle α of the above-described configuration is more than 30°, the state in which the steel wire is sandwiched between the pair of rollers becomes unstable, so that the steel wire in the conveyance rotates, and the apex of the rectangular shape in the cross-sectional shape of the steel wire The portion becomes a state in which it is in contact with the pair of rollers of the pinch roller. In this case, there is a case where the apex portion of the rectangular shape in the cross-sectional shape of the steel wire is broken or the steel wire is broken.

Further, when the pinch roller is not disposed, the steel wire is not deformed by the stress from the pinch roller. However, when the pinch rolls are not disposed, the steel wire is rotated and twisted when the steel wire is taken up on the cylindrical drum, so that the adjacent steel wires wound around the cylindrical drum are easily viewed from each other in cross section. Become a state of point contact. Therefore, the cross-sectional shape of the steel wire may be deformed due to the tension at the time of winding, or the steel wire may be flawed.

In the cross-sectional shape shown in FIG. 3, since the angle α of the above-described configuration is 30° or less, it is difficult for the stress from the pinch roller to concentrate on the apex portion of the rectangular shape in the cross-sectional shape of the steel wire. Therefore, it is difficult for the apex portion of the rectangular shape in the cross-sectional shape of the steel wire to be broken and deformed, or the steel wire is hard to be produced.

Further, when the angle α of the above configuration is 30 or less, the state in which the steel wire is sandwiched between the pair of rollers is stabilized. Therefore, the wire loop fastener after winding is likely to be in contact with the first straight portion 51a of the adjacent steel wire and the second straight portion 52a. Therefore, by setting the angle of the above configuration to 30 or less, it is possible to effectively prevent the steel wire after the strand annealing from being broken or deformed or flawed.

Further, in order to more effectively prevent breakage or flaws in the steel wire, the angle of the above configuration is preferably 15 or less, and most preferably 0 (the second straight portion 52a of the second side 52 is parallel to the first straight portion 51a).

Further, in the steel wire shown in FIG. 3, the first dimension (T) which is the largest dimension of the cross-sectional shape in the direction orthogonal to the first straight portion 51a and the direction parallel to the first straight portion 51a The ratio (T/W) of the second dimension (W) of the largest dimension of the cross-sectional shape is set to 3 or less. When the ratio (T/W) exceeds 3, the state in which the steel wire is sandwiched between the pair of rollers becomes unstable. When the ratio (T/W) is 3 or less, the state in which the steel wire is sandwiched between the pair of rolls is stabilized, and damage or flaws of the steel wire can be prevented. The ratio (T/W) is preferably 1.5 or less, more preferably 1 or less, in order to further stabilize the state in which the steel wire is sandwiched between the pair of rolls, and to prevent the steel wire from being broken or smashed more effectively.

Further, the length L1 of the first side 51 of the steel wire system shown in Fig. 3 (the same as the maximum dimension (W) in the direction parallel to the first straight portion 51a in Fig. 3) is the length L2 or more of the second side 52. The length L1 of the first side 51 and the length L2 of the second side 52 of the second dimension (W) are each in the range of W/10 to W. When the length L1 of the first side 51 and the length L2 of the second side 52 are less than W/10, respectively, the state in which the steel wire is sandwiched between the pair of rollers becomes unstable. When the length L1 of the first side 51 and the length L2 of the second side 52 are within the above range, the state in which the steel wire is sandwiched between the pair of rolls is stabilized, and damage or flaws of the steel wire can be prevented. In order to more effectively prevent damage or flaws in the steel wire, the length L1 of the first side 51 and the length L2 of the second side 52 are preferably W/5 to W.

Here, the steel wire loop fastener is preferably a steel wire in which the cross-sectional shape shown in Fig. 3 is taken up. Therefore, at the time of manufacture, even if the pair of rollers in which the pinch rollers are disposed facing each other are in contact with the first straight portion 51a and the second straight portion 52a, the steel wire passes through the pair of the rollers sandwiched between the pinch rolls. The stress from the pinch rolls is also difficult to concentrate on the apex portion of the rectangle in the cross-sectional shape of the steel wire. Further, the steel wire loop is in a state in which the state in which the steel wire is sandwiched between the pair of rollers is stabilized. Therefore, the wire loop fastener after winding is likely to be in contact with the first straight portion 51a of the adjacent steel wire and the second straight portion 52a.

As described above, such a steel wire loop buckle is a producer which can suppress the destruction or flaw of the cross-sectional shape of the steel wire at the time of manufacture. Moreover, the steel wire loop fastener comprises a steel wire which can be used as a soft profiled cross-sectional shape of a near-net-formed stainless steel wire, and is therefore suitable for a super-shaped complex shape. The formation of magnetic parts.

The cross-sectional shape of the steel wire wound around the steel wire loop is not limited to the one illustrated in FIG.

4(a) to 4(c) are cross-sectional views exemplarily showing cross-sectional shapes of other steel wires.

The cross-sectional shape of the steel wire shown in Fig. 4(a) is different from the cross-sectional shape of the steel wire shown in Fig. 3 only in that the concave portion C1 is formed in the first side 51B and the concave portion C2 is formed in the second side 52B. Therefore, members that are the same as those in FIG. 3 in FIG. 4(a) are denoted by the same reference numerals and will not be described.

The concave portion shown in FIG. 4(a) may be formed on either the first side 51B and the second side 52B, or may be formed only in one of the first side 51B or the second side 52B. Further, the concave portion may be provided on the third side 53 and/or the fourth side 54. Further, the number of the recesses existing in each side may be one as shown in FIG. 4(a), or two or more.

In the steel wire of the cross-sectional shape shown in Fig. 4 (a), the first side 51B is formed by the first side member 51b and the second side member 51c which extend on the same straight line via the concave portion C1. The length of the first side member 51b and the second side member 51c may be the same or different.

The recess C1 having a width of W/10 or more does not contribute to the contact of the adjacent steel wires in the wound state or the contact of the pair of rollers of the pinch roller with the first straight portion 51a. Therefore, as shown in FIG. 4(a), when the concave portion C1 having a width of W/10 or more is formed on the first side 51B, the width dimension LC1 of the concave portion C1 is not included in the length L1 of the first side 51B. Therefore, the length L1 of the first side 51B in the cross-sectional shape shown in Fig. 4(a) is a total of the length L1b of the first side member 51b extending in the same straight line and the length L1c of the second side member 51c. length.

In the steel wire of the cross-sectional shape shown in Fig. 4 (a), the second side 52B is formed by the first side member 52b and the second side member 52c which extend on the same straight line via the concave portion C2. The length of the first side member 52b and the second side member 52c may be the same or different.

The recess C2 having a width of W/10 or more does not contribute to the contact of the adjacent steel wires in the wound state or the contact of the pair of rollers of the pinch roller with the second straight portion 52a. Therefore, when the concave portion C2 having a width dimension of W/10 or more is formed on the second side 52B, the concave portion is formed. The width dimension LC2 of C2 is not included in the length L2 of the second side 52B. Therefore, the length L2 of the second side 52B in the cross-sectional shape shown in Fig. 4(a) is a total of the length L2b of the first side member 52b extending in the same straight line and the length L2c of the second side member 52c. length.

Further, when the width of the concave portions C1 and C2 in the cross-sectional shape is less than W/10, even if the concave portion is formed in the first side 51B and/or the second side 52B, the adjacent state of the winding state can be ignored. The influence of the steel wire on each other. Further, when the widths of the recesses C1 and C2 in the cross-sectional shape are less than W/10, it is also possible to ignore the pair of roller pairs in which the pinch rollers are disposed opposite to each other, and the second straight portion 51a and the second straight portion are also contacted. The effect of the stability of the state of 52a. Therefore, when the width dimension of the concave portion C1 in the cross-sectional shape is less than W/10, the width dimension of the concave portion C1 is included in the length L1 of the first side 51B. Further, when the width dimension of the concave portion C2 in the cross-sectional shape is less than W/10, the width dimension of the concave portion C2 is included in the length L2 of the second side 52B.

The steel wire of the cross-sectional shape shown in Fig. 4 (a) includes the first side 51B having the first straight portion 51a and the first straight portion 51a inclined at an angle (α) of 30 or less with respect to the first straight portion 51a. The straight portion 51a faces the second side 52B of the second straight portion 52a disposed. Further, the steel wire of the cross-sectional shape shown in Fig. 4 (a) is the first dimension (T) of the largest dimension in the direction orthogonal to the first straight portion 51a of the cross-sectional shape, and the first dimension as the cross-sectional shape. The second dimension (W) of the largest dimension in the direction in which the straight portions 51a are parallel (in FIG. 4, the length L1b of the first side member 51b, the width dimension LC1 of the recess C1, and the length L1c of the second side member 51c are totaled The ratio (T/W) of the obtained length) is 3 or less. Further, the length L1 of the first side 51B of the steel wire system of the cross-sectional shape shown in Fig. 4(a) is equal to or longer than the length L2 of the second side 2B, and the length L1 of the first side 51B with respect to the second size (W). And the length L2 of the second side 52B is in the range of W/10 to W, respectively.

Therefore, in the steel wire loop which is wound with the steel wire having the cross-sectional shape shown in Fig. 4 (a), it can be suppressed in the same manner as the steel wire loop fastener which winds the steel wire of the cross-sectional shape shown in Fig. 3 Destruction or smashing of the cross-sectional shape of the steel wire at the time of manufacture.

Further, the steel wire of the cross-sectional shape shown in Fig. 4(a) is formed on the first side 51B to form the concave portion C1 and Since the concave portion C2 is formed in the second side 52B, the steel wire loop fastener in which the steel wire having the cross-sectional shape shown in Fig. 4(a) is wound is suitably used as a near-net-formed stainless steel wire such as a cable joint.

Further, in the cross-sectional shape of the steel wire wound around the steel wire loop, the first side member and the second side member of the first side (and/or the second side) may be the same as shown in FIG. 4(a) Extending straight, it can also extend on different straight lines as shown in Figure 4(b) and Figure 1(c).

In the cross-sectional shape shown in FIG. 4(b), the first side member 80b of the first side 80B is parallel to the second side member 80c. In this case, the dimension d1 between the position in the extending direction of the first side member 80b and the position in the extending direction of the second side member 80c in the direction orthogonal to the first straight portion 51a is the first size ( 1/10 or less of T), even if the first side member 80b of the first side 80B and the second side member 80c are extended on different straight lines, the same effect as the cross-sectional shape of Fig. 4(a) can be obtained.

4(b), the first side member 80b of the first side 80B and the second side member 80c are extended on different straight lines, but the first side member and the second side of the second side are exemplified. The two side members can also extend on different straight lines. When the first side member and the second side member of the second side extend in different directions, and the first side member is parallel to the second side member, the direction perpendicular to the first straight portion 51a is The dimension between the position in the extending direction of the first side member of the second side and the position in the extending direction of the second side member is 1/10 or less of the first dimension (T), and is obtained as shown in FIG. 4 (a). ) The effect of the same cross-sectional shape.

Further, as shown in FIG. 4(c), the first side member 80b and the second side member 80c of the first side 80B extend on different straight lines via the recess C1, and the first side member 80b and the second side member are extended. When 80c is not parallel, if the angle θ of the extending direction of the second side member 80c with respect to the extending direction of the first side member 80b is 30 or less, the same effect as the cross-sectional shape of Fig. 4(a) can be obtained. . That is, as shown in FIG. 4(c), the first side member 80b and the second side member 80c are relatively biased toward the method of forming a mountain, and may be relatively biased toward the direction in which the valley is formed.

In the case where the first side member 80b and the second side member 80c are not parallel, the extending direction of the first straight portion 51a means that the first side member 80b and the second side member 80c are longer. The extending direction of the side member (the second side member 80c in Fig. 4(c)). In addition, when the length of the first straight portion 51a is the same as the length of the first side member and the second side member, the second dimension when the first side member and the second side member are used as the reference are used. (W) The direction in which the side member having the second dimension is measured is extended.

In addition, in FIG. 4(c), the first side member 80b and the second side member 80c of the first side 80B are extended on different straight lines, and the first side member 80b and the second side of the first side 80B are extended. The side members 80c are not parallel, but the first side members and the second side members of the second side may be non-parallel extending on different straight lines. In this case, when both the first side member and the second side member of the second side are inclined by 30 or less with respect to the extending direction of the first straight portion 51a, the same effect as the cross-sectional shape of FIG. 4(a) can be obtained.

In the case where there are two or more straight lines facing the first straight portion 51a, the second straight portion 52a is determined based on the following (1) to (4).

(1) When there is one straight line inclined at 30° or less with respect to the first straight portion 51a, the straight line is referred to as the second straight portion 52a.

(2) When there are a plurality of straight lines inclined at 30° or less with respect to the first straight portion 51a, the straight line having the longest length is referred to as the second straight portion 52a.

(3) When there are a plurality of straight lines inclined at 30° or less with respect to the first straight portion 51a and two or more straight lines have the longest length, the difference between the angles of the first straight portions 51a and the first straight portions 51a is minimized. The straight line is set as the second straight portion 52a.

(4) There are a plurality of straight lines that are inclined at 30° or less with respect to the first straight portion 51a, and two or more straight lines have the longest length, and the straight line having the smallest difference between the angles of the first straight portions 51a and the first straight portions 51a exists. In the case of a strip or more, any one of the straight lines may be used as the second straight portion 52a.

Fig. 5 is a cross-sectional view showing another example of the cross-sectional shape of the steel wire. The cross-sectional shape of the steel wire shown in Fig. 5 differs from the cross-sectional shape shown in Fig. 3 in that both ends of the sides 51C, 52C, 53C, and 54C are curved and the sides and the sides are connected by a smooth curve.

The first side 51C shown in Fig. 5 has a first straight portion 91a disposed at the center in the longitudinal direction. Further, the second side 52C has a second straight portion 92a disposed at the center in the longitudinal direction. The first straight portion 91a and the second straight portion 92a are arranged to face each other. Similarly to the cross-sectional shape shown in FIG. 3, the second straight portion 92a is inclined at an angle (α) of 30° or less with respect to the first straight portion 91a.

Further, in the cross-sectional shape shown in FIG. 5, the first dimension (T) which is the largest dimension in the direction orthogonal to the first straight portion 91a and the direction parallel to the first straight portion 91a which is the cross-sectional shape are parallel. The ratio (T/W) of the second dimension (W) of the largest dimension is also 3 or less.

As shown in FIG. 5, when one end portion or both end portions of the first side 51C (and/or the second side 52C) are curved, the following contact ranges 91b, 91c, 92b, 92c in the curve have the following functions. : Advancing the surface of the adjacent steel wires in a state of being wound up, and improving the stability of the state in which the steel wire is sandwiched between the pair of rollers of the pinch rolls.

Therefore, in the first side 51C shown in FIG. 5, the total length of the length L91a of the first straight portion 91a and the lengths L91b and L91c of the contact ranges 91b and 91c of the curve is referred to as the length L1 of the first side 51C. Further, in the second side 52C shown in FIG. 5, the total length of the length L92a of the second straight portion 92a and the lengths L92b and L92c of the contact ranges 92b and 92c of the curve is referred to as the length L2 of the second side 52C.

The curved contact regions 91b and 91c (92b, 92c) are drawn at 30° from the end of the first straight portion 91a (or the second straight portion 92a) with respect to the first straight portion 91a (or the second straight portion 92a). The straight line whose angle is inclined, the intersection of the straight line and the curve to the end of the first straight portion 91a (or the second straight portion 92a).

In the cross-sectional shape shown in FIG. 5, the length L1 of the first side 51C is equal to or longer than the length L2 of the second side 52C, and the length L1 and the second side 52C of the first side 51C of the second dimension (W). The length L2 is in the range of W/10 to W, respectively.

The steel wire having the cross-sectional shape shown in FIG. 5 includes a first side 51C having the first straight portion 91a and a first straight portion inclined at an angle (α) of 30° or less with respect to the first straight portion 91a. The second side 52C of the second straight portion 92a that is disposed opposite to the 91a is formed as a cross-sectional shape Ratio of the first dimension (T) of the largest dimension in the direction orthogonal to the first straight portion 91a to the second dimension (W) of the largest dimension in the direction parallel to the first straight portion 91a of the cross-sectional shape (T) /W) is 3 or less, and the length L1 of the first side 51C is equal to or longer than the length L2 of the second side 52C, and the length L1 of the first side 51C and the length L2 of the second side 52C of the second dimension (W) are respectively It is the range of W/10~W.

Therefore, in the steel wire loop fastener in which the steel wire of the cross-sectional shape shown in FIG. 5 is wound, the same can be suppressed as in the case of the steel wire loop fastener wound with the steel wire of the cross-sectional shape shown in FIG. The destruction of the cross-sectional shape of the steel wire or the occurrence of defects.

Further, the steel wire of the cross-sectional shape shown in FIG. 5 is formed by joining the sides 51C, 52C, 53C, and 54C by a smooth curve, so that the stress from the pinch rolls is hard to be further concentrated on the cross-sectional shape of the steel wire. The vertices in the middle. Moreover, the state in which each pair of rollers in which the pinch rollers are disposed in contact with the first straight portion 91a and the second straight portion 92a is further stabilized. Therefore, the steel wire loop fastener which winds the steel wire of the cross-sectional shape shown in FIG. 5 can further suppress the destruction of the cross-sectional shape of the steel wire at the time of manufacture, or the generation of the flaw.

Further, the shape of the steel wire constituting the steel wire loop fastener of the present invention is not limited to the cross-sectional shape shown in FIGS. 3 to 5, and various modifications can be made without departing from the scope of the invention.

Next, a method of manufacturing a steel wire loop will be described.

In the manufacture of a steel wire loop, first, a wire having the above-described composition is subjected to a wire drawing process to form any of the profiled cross-sectional shapes of FIGS. 3 to 5, and a strand annealing is performed to form a steel wire. The wire drawing ratio of the wire drawing process is preferably 10 to 95% as described above. Further, as described above, the annealing temperature in the strand annealing is preferably 900 to 1200 ° C, and the annealing time is preferably 5 seconds to 24 hours.

In the method for producing such a steel wire loop fastener, after the strand annealing is performed, the steel wire is taken up by a pinch roller. When the steel wire is passed through the pinch roller, the pair of rollers in which the pinch rollers are disposed are placed so as to pass through the steel wire so as to contact the first straight portion of the first side and the second straight portion of the second side. Then, by means of a pinch roller, one side of the cylindrical drum wound with a steel wire The surface is controlled to be conveyed in the direction in which the first straight portion or the second straight portion of the steel wire opposes, and the steel wire is conveyed to the cylindrical drum for winding. Thereby, in this method, the destruction of the cross-sectional shape of the steel wire at the time of manufacture or the generation of a flaw is suppressed.

Here, before the steel wire after the strand annealing is passed through the pinch rolls, a skin pass process may be performed in order to correct the cross-sectional shape or the introduction and transfer.

Further, in the case where the cross-sectional shape of the steel wire is circular, the destruction of the cross-sectional shape of the steel wire at the time of manufacture or the occurrence of flaws does not become a problem. Therefore, in the case where the cross-sectional shape of the steel wire is circular, it is also possible to use any of the previously known methods to wind up the steel wire to form a steel wire loop fastener.

Example

(Test Example 1)

A wire which can be used in the metal part for a fastening member of the present invention was produced, and tensile strength, tensile reduction of the section, cold workability, corrosion resistance, and magnetic flux density of the wire were evaluated. The composition of each of the wires of the examples and the comparative examples is shown in Tables 1 to 3.

It is assumed to be melted by AOD (Argon Oxygen Decarburization) as a low-cost melting process of stainless steel, melted in a 100 kg vacuum melting furnace, and cast into a diameter of 180 mm having the composition shown in Tables 1-3. Casting. The obtained cast wire rod was heat-calendered (reduction ratio: 99.9%) to a diameter of 6 mm, and the inter-heat rolling was terminated at 1000 °C. Thereafter, it was kept at 1050 ° C for 30 minutes in a solution treatment (homogenization heat treatment), then water-cooled, and pickled to obtain a circular cross-section wire.

Further, for a part of the wire rod, in a usual steel wire manufacturing step, a steel wire having a circular cross section having a diameter of 4.2 mm is drawn, and subjected to strand annealing at 1050 ° C for 3 minutes to form a steel wire.

The tensile strength, tensile section shrinkage, cold workability, corrosion resistance, and magnetic properties of the wire and steel wire obtained in this manner were evaluated. The evaluation results are shown in Tables 4 to 6. In addition, among the various results shown in Tables 4 to 6, No. 1, 3, 5 to 76, 82 to 89, and 116 to 119 are characteristic values measured in the state of the wire, and No. 2 and 4 are related. The obtained characteristic value was measured in the state of a steel wire.

The tensile strength and tensile section shrinkage of the wire and the steel wire were measured in accordance with JIS Z2241.

The tensile strength of the steel wire within the range of the specific component composition is 650 MPa or less, and the tensile reduction ratio of the tensile section is 70% or more. In addition, it is set to Mn: more than 13.0% and 20% or less, Cu: 1.0% - 4.0%, Al: 0.01% - 1.3%, N: 0.01 or more, and less than 0.10%, and the addition amount of the component is further set. The exact amount shows a good value, ie 590 MPa Hereinafter, the shrinkage ratio of the stretched section is 75% or more.

The cold workability was evaluated by cutting a cylindrical sample having a diameter of 4 mm and a height of 6 mm from a wire or a steel wire, and performing cold compression processing (strain rate 10/s) at a processing rate of 75% in the height direction. In the shape of a flat disk, the presence or absence of cracking in the sample after compression processing and the deformation resistance during compression processing were measured.

In the case of cold compression processing in which the deformation resistance of the deformation resistance (1100 MPa) which is not broken and can be less than SUS304 is obtained, the cold workability is evaluated as ○, and in the case of occurrence of cracking or deformation resistance of SUS304 or more, cold workability evaluation is performed. For ×. In addition, when the deformation resistance equivalent to SUSXM7 (1000 MPa or less) was exhibited, the cold workability was evaluated as ◎.

The cold workability of the steel wire within the range of the specific component composition is ○ or ◎, and exhibits excellent cold workability.

Corrosion resistance was carried out according to the salt spray test of JIS Z2371, and a 100-hour spray test was carried out, and evaluation was performed based on whether or not rust was generated. Corrosion resistance was evaluated as good (○) in the case of no rust level, and corrosion resistance was evaluated as poor (x) in the case of red rust such as flow rust.

The corrosion resistance is good in the steel wire within the range of the specific component composition.

The magnetic material was subjected to a cold compression-processed sample for evaluation of cold workability, and a magnetic field of 10,000 (Oe) was applied by a DC magnetization tester, and the magnetic flux density at this time was evaluated.

The steel wire in the range of the specific component composition has a magnetic flux density of 0.01 T or less after cold compression processing, in particular, Mn: more than 13.0% and 24.9% or less, and Ni: more than 6.0%. Less than 10.0% and Md30: -167 or less showed further excellent super-nonmagnetic, that is, 0.007T or less.

Next, the hot working rate in the thermal intercalation of the wire which is partially segregated by Ni or Cu and the subsequent homogenization heat treatment temperature were investigated.

A cast piece of 180 mm in diameter of steel A and CW composed of the components shown in Table 1 or Table 2 manufactured in the same manner as the step of producing the wire shown in Table 4 or Table 5 is reduced as shown in Table 7. At the shrinkage rate, the wire was heat-rolled to either a diameter of 6 mm (reduction rate of 99.9%), a diameter of 30 mm (reduction rate of 99.0%), and a diameter of 30 mm (reduction rate of 97.0%), and the inter-heat rolling was terminated at 1000 °C. Thereafter, as a solution treatment (homogeneization heat treatment), No. 80 and 94 of Table 7 are at 900 ° C, No. 77, 81, 90, 95, 97, 99 of Table 7 are at 1050 ° C, and No. 7 is No. 78, 91, 92, 96, and 98 were held at 1150 ° C, No. 79, and 93 of Table 7 at a temperature of 1,250 ° C for 30 minutes, and then water-cooled, and pickled to obtain a circular wire having a circular cross section. In addition, for a part of the wire, in the manufacturing process of the normal steel wire, the wire is processed into a circular steel wire having a diameter of 4.2 mm, and is subjected to a strand annealing at 1050 ° C for 3 minutes to form a steel wire ( Table No. 96~99).

Then, tensile strength, tensile section shrinkage, cold workability, corrosion resistance, and magnetic properties of the obtained wire and steel wire were evaluated in the same manner as above. Further, the standard deviation of the segregation of Ni and Cu in the steel material and the steel wire was calculated by the following method. The evaluation results are shown in Table 7. In addition, among the various results shown in Table 7, the characteristic values measured in the state of the wire in No. 77-81 and 90-95 are related to the characteristic values measured in the steel wire state of No. 96-99. . The various characteristic values of the steel wire were measured in the same manner as the above-mentioned wire.

The standard deviation of the Ni concentration and the Cu concentration of the wire or the steel wire (the standard deviation σ of the unevenness of the center portion in the cross section) was calculated as follows. First, an arbitrary portion of a region surrounded by a circle having a radius of 1/4 of the diameter of the wire or the steel wire from the center of the cross section of the wire or the steel wire was analyzed by EPMA analysis and evaluated. In the EPMA analysis, the concentration of Ni and Cu was measured at a measurement position of 200 dots in the vertical direction and 200 dots in the grid at a pitch of 1 μm, and the standard deviation σ of the unevenness of the Ni concentration and the Cu concentration was determined.

As shown in Table 7, the standard deviation of Ni segregation is 5% when the hot working ratio of the wire (shrinkage ratio of the hot rolling of the wire) is 99% or more and the heat treatment temperature is 1000 to 1200 °C. Hereinafter, the standard deviation of Cu segregation is 1.5% or less, and good cold workability and super non-magnetic properties can be obtained.

Next, annealing was performed to investigate the influence of the profile shape of the steel wire on the shape fracture after the strand annealing in order to obtain a steel wire loop buckle of a profiled cross-sectional shape that was soft and unbroken.

A cast piece of 180 mm in diameter of steel A and CW composed of the components shown in Table 1 or Table 2 manufactured in the same manner as the step of producing the wire shown in Table 4 or Table 5 was carried out at a reduction ratio of 99.9%. The wire was calendered to a diameter of 6 mm and the inter-heat rolling was terminated at 1000 °C. Thereafter, it was kept at 1050 ° C for 30 minutes as a solution treatment (homogeneization heat treatment), then water-cooled, and pickled to obtain a wire having a circular cross section.

A profiled wire having a circular shape of 6 mm in diameter was subjected to profiled wire rolling (stretching process), and a profiled shape having a cross-sectional shape as shown in FIG. 3 and varying the size of each portion as shown in Table 8 was used. The steel wire of the shape was formed, and thereafter, it was subjected to a strand annealing at 1050 ° C for 3 minutes, and then coiled by a method shown below to obtain a steel wire loop fastener.

In Table 8, "T" is the largest dimension in the direction orthogonal to the first straight portion of the cross-sectional shape, and "W" is the largest dimension in the direction parallel to the first straight portion of the cross-sectional shape. "α" is an angle formed by the first straight portion 1a and the second straight portion 2a. "L1" is the length of the first side 1, and "L2" is the length of the second side 2. As the winding method, each of the pinch rolls is disposed in parallel with each other The roller pair passes through the steel wire so as to contact the first straight portion 51a and the second straight portion 52a, and winds while controlling the conveyance direction of the steel wire.

For the steel wire of the steel wire loop, it was visually evaluated (shape evaluation) whether the cross-sectional shape was broken or not. Then, the case where the damage or flaw was present was evaluated as ×, the case where there was no damage was evaluated as ○, and the case where both damage and flaws existed was evaluated as ◎. The evaluation results are shown in Table 8.

As shown in Table 8, when either of T/W, α, and L1 is outside the range of the present invention, the steel wire of the steel wire buckle is broken or flawed, and the shape is evaluated as ×.

As can be seen from Table 8, the cross-sectional shape of the steel wire of the steel wire loop is set to the following cross-sectional shape, which is α≦30°, T/W is 3 or less, and L1 and L2 are W/10~. The range of W can suppress the damage or flaw of the cross-sectional shape of the steel wire.

(Test Example 2)

Secondly, it is made of stainless steel in the metal parts for the fastening parts which can be used in the invention. The hardness, tensile strength and elongation of the processed material (Y rod) were evaluated, and the pair of fastener elements were meshed with each other by the stainless steel, and the needle inspection performance was evaluated. Description.

Table 9 shows the composition of the stainless steel used in the metal wire and the chain.

Each of the chain of 20 cm in length and 40 cm in chain length was separately produced by each of Examples 1, 2 and Comparative Examples 1 and 2 having the composition shown in Table 9, and each of the trial-made chains was made. As shown by the arrow in the figure, the change in the magnetic flux density generated at this time was measured by the needle detector (APA-6000, manufactured by SANKO Electronics Research Co., Ltd.) shown in a plan view in Fig. 6 in a direction perpendicular to the advancing direction. Amount as a needle value, and as a relative Ratio of iron balls of 1.5 mm 1.5 iron balls are compared to them. The results are shown in Table 10. Table 10 1.5 The smaller the value of the iron ball is, the more difficult it is to detect it by the needle detector, and the point of preventing the malfunction is that the needle detection performance is excellent.

Further, in the results shown in Table 10, the degree of tempering H is based on the case where the fastener element is formed, and the heat treatment is not performed during the cold working of the processed material, and the degree of tempering H/2 is applied to the cold working of the processed material ( In the middle of the rolling process, the intermediate heat treatment is performed, and the degree of tempering is performed by heat treatment after the cold working (calendering) of the processed material, and then the fastener element is attached to the chain cloth.

According to the results shown in Table 10, the case where the chain length was 20 cm and 40 cm was due to the tempering degree H of Comparative Example 1 and the tempering degree of Comparative Example 1 1.5 The iron ball is too large to be measured, which makes it impossible to measure. In contrast, it can be clarified that Examples 1 and 2 1.5 Iron balls are sufficiently less than 100% than any of the tempering degrees.

Further, for each of Example 1 and Comparative Examples 1 and 2, the cross-sectional hardness, tensile strength, and elongation of the processed material produced in the case of each of the tempering degrees H, H/2, and O were measured. The results are shown in Table 11. The smaller the values of the hardness and the tensile strength of the cross-section, the more excellent the workability, which means that the manufacturing efficiency can be improved.

Further, the intermediate heat treatment of the degree of tempering H/2 is carried out under the same conditions as the homogenization heat treatment previously described (temperature: 1000 to 1200 ° C).

As shown in Table 11, in the case of comparison between each of the tempering degrees H, H/2, and O, the hardness and tensile strength of Example 1 were smaller than those of Comparative Example 2. Regarding the elongation, Example 1 has an elongation of 1% or more in any degree of tempering.

Therefore, according to the metal part for a fastening member of the present invention, it is understood that it has non-magnetic properties which does not cause a malfunction of the needle detector, and productivity can be improved.

1‧‧‧ zipper

2‧‧‧Chain row

2a‧‧‧ sprocket

3‧‧‧Chain

3a‧‧‧ core

4‧‧‧Sliding parts

5‧‧‧Upstop

6‧‧‧Next stop

Claims (14)

A metal part for a fastening component, which is C: 0.08% or less, Si: 0.05% to 2.0%, Mn: more than 8.0% and 25.0%, P: 0.06% or less, S: 0.01%, by mass% Hereinafter, Ni: more than 6.0% and 30.0% or less, Cr: 13.0% to 25.0%, Cu: 0.2% to 5.0%, N: less than 0.20%, Al: 0.002 to 1.5%, and C+N less than 0.20% The remainder contains Fe and unavoidable impurities, and Md30 represented by the following formula (a) is set to -150 or less, and Md30 = 413-462 (C + N) - 9.2 Si - 8.1 Mn - 9.5 Ni -13.7Cr-29Cu (a) wherein the element symbol in the formula (a) means the content (% by mass) of the element. If the fastening component of claim 1 is a metal part, the magnetic flux density displayed in a magnetic field of 10,000 oersted is 0.01 T or less. If the fastening component of claim 1 or 2 is a metal part, it is subjected to cold working, cold working and heat treatment. A metal part for a fastening member according to claim 1 which is contained in mass%, further contains 3.0% or less of Mo, and Md30 represented by the following formula (b) instead of Md30 represented by the above formula (a) 'Set to -150 or less, Md30' = 413-462 (C+N) - 9.2Si-8.1Mn-9.5Ni-13.7Cr-18.5Mo-29Cu (b). The metal component for the fastening component of claim 1 is made of at least one selected from the group consisting of Nb, V, Ti, W, and Ta in an amount of 1.0% by mass or less. The metal part for the fastening component of claim 1 is made of a mass %, and further contains 3.0% or less of Co. The metal component is used for the fastening component of claim 1 in an amount of % by mass, and further contains 0.015% or less of B. The metal component for the fastening component of claim 1 is further contained in a mass %, and further contains at least one selected from the group consisting of Ca: 0.01% or less, Mg: 0.01% or less, and REM: 0.05% or less. A zipper comprising a zipper 1 constituting a part, the constituting part comprising a pair of sprocket 2a, a pair of sprocket rows 2, and a chain of the sprocket 2 The teeth 2a are meshed or separated from each other to be slidably displaced along the element row 2, and the fastener elements 2a of the fastener elements 2 are formed by the fastener elements 2a as claimed in claims 1 to 8 The fasteners of any one are made of metal parts. A zipper of claim 9, which has an iron ball value Needle performance below 1.5mm. A method of manufacturing a metal part for a fastening component, which is a cold working of a wire or a steel wire having a specific composition when the metal component for a fastening component according to any one of claims 1 to 8 is manufactured. The wire or steel wire is formed into a processed material including a rectangular wire and/or a profiled wire, and thereafter, the processed material is subjected to cold working. The method for producing a metal part for a fastening member according to claim 11, wherein the cross-sectional hardness of the processed material is 220 to 360 in terms of Vickers hardness HV, and the elongation of the processed material is 1% or more. The method for producing a metal part for a fastening member according to claim 11, wherein the tensile strength of the processed material is in the range of 450 MPa to 1100 MPa. The method of producing a metal part for a fastening member according to any one of claims 11 to 13, wherein the heat treatment is performed during the cold working of the processed material.